Magneto-optical recording medium and a method of recording and/or reproducing using the same

ABSTRACT

A magneto-optical recording medium including a base; a readout layer formed on the base; a recording layer formed on the readout layer; and an auxiliary recording layer formed on the recording layer, each of the readout layer, recording layer and auxiliary recording layer being made of an alloy of rare-earth metal and transition metal showing ferrimagnetism. The alloy composition of each layer is determined so that the recording layer has a Curie temperature lower than Curie temperatures of the readout layer and the auxiliary recording layer and has a coercive force higher than coercive forces of the readout layer and the auxiliary recording layer at room temperature and that, when the temperature of the recording layer is raised to near its Curie temperature while perpendicularly applying a uniform recording magnetic field to each layer, a sublattice magnetic moment of the rare-earth metal of the readout layer and a sublattice magnetic moment of the rare-earth metal of the auxiliary recording layer are antiparallel to each other. And, a method of recording information on the magneto-optical recording medium. This structure enables overwriting by light-intensity modulation without using an initializing magnetic field.

FIELD OF THE INVENTION

The present invention relates to magneto-optical recording media such asmagneto-optical disks, tapes and cards, for use in a magneto-opticalrecording device, and a method of recording and/or reproducing usingsuch a magneto-optical recording medium.

BACKGROUND OF THE INVENTION

Magneto-optical disk memories are put to practical use as rewritableoptical disk memories.

However, the magneto-optical disk memories suffer from a disadvantage inrewriting. Namely, it takes time to rewrite information. When writinginformation again in a portion containing information, there is a needto erase the previously recorded information before performing therewriting.

In order to overcome such a disadvantage, overwriting by magnetic-fieldmodulation is used as a method for overwriting without performingerasing before rewriting.

In the case of using this method, however, the following disadvantagesarise. Since the overwriting is performed by modulating the magneticfield strength, it is necessary to bring a magnetic field generatingmechanism close to a magneto-optical disk to obtain a magnetic field ofa sufficient strength. Additionally, with this method, a magnetic fieldcannot be modulated at high speeds.

In order to overcome such disadvantages, Japanese Publication forUnexamined Patent Application No. 175948/1987 proposes a magneto-opticalrecording medium having a double-layer structure including a recordinglayer and auxiliary recording layer, both of which are made by aperpendicularly magnetized film, and a light-intensity modulationoverwriting method capable of performing overwriting on themagneto-optical recording medium by modulating only laser power.

With the above-mentioned conventional structures, however, the directionof magnetization of the auxiliary recording layer is changed whenperforming overwriting. It is thus necessary to execute initializationin order to set the direction of magnetization of the auxiliaryrecording layer uniform in advance whenever performing the overwriting.An initializing magnetic-field generating mechanism is required inaddition to a recording magnetic field generating mechanism, resultingin increases in the size of the magneto-optical recording device and thecosts.

Moreover, if the diameter of a recording bit and the interval betweenrecording bits become smaller than the diameter of a light spot formedby focusing laser light on the recording medium, adjacent recording bitsenter the light spot. It is therefore impossible to reproduce a singlerecording bit.

SUMMARY OF THE INVENTION

An object of the present invention is to provide a magneto-opticalrecording medium permitting overwriting by light-intensity modulationwithout using an initializing magnetic field, and a recording method.

In order to achieve the above object, a magneto-optical recording mediumof the present invention includes:

a substrate;

a readout layer formed on the substrate;

a recording layer formed on the readout layer;

an auxiliary recording layer formed on the recording layer, each of thereadout layer, recording layer and auxiliary recording layer being madeof an alloy of rare-earth metal and transition metal showingferrimagnetism,

wherein an alloy composition of each layer is determined so that therecording layer has a Curie temperature lower than Curie temperatures ofthe readout layer and the auxiliary recording layer and has a coerciveforce higher than coercive forces of the readout layer and the auxiliaryrecording layer at room temperature and that, when the recording layeris raised to a temperature near its Curie temperature whileperpendicularly applying a uniform recording magnetic field to eachlayer, a sublattice magnetic moment of the rare-earth metal of thereadout layer and a sublattice magnetic moment of the rare-earth metalof the auxiliary recording layer are antiparallel to each other.

With this structure, when a temperature is raised to near the Curietemperature of the recording layer, the direction of magnetization ofthe recording layer is determined by the balance among a magnetostaticcoupling force for aligning the direction of magnetization of therecording layer with the direction of a recording magnetic field, anexchange coupling force for aligning the sublattice magnetic moment ofthe readout layer with the sublattice magnetic moment of the recordinglayer and an exchange coupling force for aligning the sublatticemagnetic moment of the auxiliary recording layer with the sublatticemagnetic moment of the recording layer. The alloy composition of eachlayer is determined such that, when the recording layer is raised to atemperature in the vicinity of its Curie temperature while applying auniform recording magnetic field thereto, the sublattice magnetic momentof the rare-earth of the readout layer and that of the auxiliaryrecording layer become antiparallel to each other. Therefore, if thepower of the laser light is modulated, a change is produced in thetemperature distribution in a direction perpendicular to each layer whenthe temperature is raised or lowered. This flips the direction ofmagnetization determined by the balance among the above-mentionedforces, and thereby allowing overwriting by light-intensity modulation.

In order to achieve the above object, a method of recording informationon the magneto-optical recording medium according to the presentinvention applies the laser light to each layer of the magneto-opticalrecording medium after modulating laser light power between high and lowaccording to information to be recorded while perpendicularly applying auniform recording magnetic field to each layer, and controls an exchangecoupling force between the recording layer and the readout layer and anexchange coupling force between the recording layer and the auxiliaryrecording layer to cause the recording layer to have upwardmagnetization or downward magnetization according to the laser lightpower.

This structure allows the light-intensity modulation overwriting on themagneto-optical recording medium.

Another object of the present invention is to provide a magneto-opticalrecording medium which permits overwriting by light-intensity modulationwithout using an initializing magnetic field and super-resolutionreadout, and a method of recording and reproducing information on themagneto-optical recording medium.

In order to achieve the above object, a magneto-optical recording mediumof the present invention has the above-mentioned structure and therecording layer whose alloy composition is determined to make thesublattice magnetic moment of the rare-earth metal of the readout layerand that of the auxiliary recording layer antiparallel to each other.

The magneto-optical recording medium of this structure has functions andeffects which are similar to those of the above-mentionedmagneto-optical recording medium. With this structure, if the intensityof the laser light is adjusted to cause only a center portion of an areaexposed to a spot of the laser light to have perpendicularmagnetization, it is possible to reproduce a recording bit which issmaller than the diameter of a laser spot. The recording density is thusimproved.

In order to achieve the above object, a recording and reproducing methodof the present invention is designed to record and reproduce informationon the magneto-optical recording medium. With this method, recording isperformed by applying the laser light to each layer of themagneto-optical recording medium after modulating laser light powerbetween high and low level according to information to be recorded whileperpendicularly applying a uniform recording magnetic field to eachlayer, and by controlling an exchange coupling force between therecording layer and the readout layer and an exchange coupling forcebetween the recording layer and the auxiliary recording layer to causethe recording layer to have upward magnetization or downwardmagnetization according to the laser light power. With this method,information is indirectly reproduced from the recording layer byapplying through the substrate the laser light of a power which is lowerthan the low power for recording and is capable of causing only a centerportion of an area of the readout layer exposed to the laser light tohave perpendicular magnetization so as to cause a sublattice magneticmoment of the rare-earth metal at the center portion to take up a stableorientation with respect to a sublattice magnetic moment of therare-earth metal of the recording layer and by reading a direction ofmagnetization of the center portion using the polar Kerr effect.

This structure enables the light-modulation overwriting and areproduction of a recording bit which is smaller than the laser spot onthe magneto-optical recording medium.

For a fuller understanding of the nature and advantages of theinvention, reference should be made to the ensuing detailed descriptiontaken in conjunction with the accompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 through FIG. 10 show the first embodiment of the presentinvention.

FIG. 1 is an explanatory view showing a schematic structure of amagneto-optical recording medium.

FIG. 2 is a graph showing an example of the temperature dependence ofcoercive force of each of the layers of the magneto-optical recordingmedium of FIG. 1 when each of these layer is formed alone.

FIG. 3 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 1 have magnetic properties shown in FIG. 2.

FIG. 4 is a graph showing the temperature dependence of coercive forceof each of the layers of FIG. 2 when the layers are laminated.

FIG. 5 is a graph showing the relationship between hysteresis propertiesof the polar Kerr rotation angle produced by a magnetic field in thelayers shown in FIG. 2 and and temperatures.

FIG. 6 is an explanatory view showing another process of recording andreproducing information on the magneto-optical recording medium of FIG.1.

FIG. 7 is a graph showing another example of the temperature dependenceof coercive force of each of the layers of the magneto-optical recordingmedium of FIG. 1 when each of these layers is formed alone.

FIG. 8 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 1 have magnetic properties shown in FIG. 7.

FIG. 9 is a graph showing another example of the temperaturedependence-of coercive force of each of the layers of themagneto-optical recording medium of FIG. 1 when each of these layers isformed alone.

FIG. 10 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 1 have magnetic properties shown in FIG. 9.

FIG. 11 through FIG. 19 show the second embodiment of the presentinvention.

FIG. 11 is an explanatory view showing a schematic structure of amagneto-optical recording medium.

FIG. 12 is a graph showing an example of the temperature dependence ofcoercive force of each of the layers of the magneto-optical recordingmedium of FIG. 11 when each of these layers is formed alone.

FIG. 13 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 11 have magnetic properties shown in FIG. 12.

FIG. 14 is a graph showing the temperature dependence of coercive forceof each of the layers of FIG. 12 when the layers are laminated.

FIG. 15 is a graph showing the relationship between hysteresisproperties of the polar Kerr rotation angle produced by a magnetic fieldin the layers shown in FIG. 12 and and temperatures.

FIG. 16 is a graph showing another example of the temperature dependenceof coercive force of each of the layers of FIG. 12 when the layers areplaced alone.

FIG. 17 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 11 have magnetic properties shown in FIG. 16.

FIG. 18 is a graph showing another example of the temperature dependenceof coercive force of each of the layers of the magneto-optical recordingmedium of FIG. 11 when each of these layers is formed alone.

FIG. 19 is an explanatory view showing a process of recording andreproducing information when the layers of the magneto-optical recordingmedium of FIG. 11 have magnetic properties shown in FIG. 18.

FIG. 20 shows a schematic structure of a magneto-optical recordingmedium according to the third embodiment of the present invention.

FIG. 21 through FIG. 31 show the fourth embodiment of the presentinvention.

FIG. 21 is an explanatory view showing a schematic structure of amagneto-optical recording medium.

FIG. 22 is a graph showing the composition dependence of Curietemperature (T_(C)) and compensation temperature (T_(comp)) of Gd_(X)(Fe₀.82 Co₀.18)_(1-X).

FIG. 23 is an explanatory view showing an example of the arrangement oflands and grooves formed on a substrate of a magneto-optical disk.

FIG. 24 is an explanatory view showing another example of thearrangement of lands and grooves formed on the substrate of themagneto-optical disk.

FIG. 25 is an explanatory view showing an example of an arrangement ofwobbly pits formed on the substrate of the magneto-optical disk.

FIG. 26 is an explanatory view showing another example of an arrangementof wobbly pits formed on the substrate of the magneto-optical disk.

FIG. 27 is an explanatory view showing an example of wobbly groovesformed on the substrate of the magneto-optical disk.

FIG. 28 is an explanatory view showing a method of recording andreproducing information on the magneto-optical disk using a plurality oflight beams.

FIG. 29 is an explanatory view showing a method of overwriting bymagnetic-field modulation on the magneto-optical disk.

FIG. 30 is an explanatory view showing a single-sided typemagneto-optical disk having the structure of FIG. 21.

FIG. 31 is an explanatory view showing a double-sided typemagneto-optical disk having the structure of FIG. 21.

FIG. 32 is a view showing a schematic structure of a magneto-opticalrecording medium according to the fifth embodiment of the presentinvention.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The following description discusses one embodiment of the presentinvention with reference to FIGS. 1 to 10.

As illustrated in FIG. 1, a magneto-optical recording medium of thisembodiment has a multi-layer structure and is formed by laminating atransparent dielectric layer 2, a readout layer 3, a recording layer 4,an auxiliary recording layer 5, a protective film 6 and an overcoat film7 in this order on a substrate 1. Recording and reproduction areperformed by focusing laser light 8 on the readout layer 3 with aconverging lens 9.

The transparent dielectric layer 2 is included to producephoto-interference effects so as to obtain improved readoutcharacteristics.

The readout layer 3, the recording layer 4 and the auxiliary recordinglayer 5 are amorphous films formed by an alloy of rare-earth metal (RE)and transition metal (TM). These layers are ferrimagnetic materials inwhich the sublattice magnetic moment of the rare-earth metal and that ofthe transition metal are antiparallel to each other. FIG. 1 shows theorientations of the sublattice magnetic moments of the rare-earth metalwith arrows.

FIG. 2 shows the temperature dependence of coercive forces of thereadout layer 3, the recording layer 4 and the auxiliary recording layer5. FIG. 4 shows the temperature dependence of coercive forces of theselayers formed on the substrate 1.

The protective film 6 (see FIG. 1) is provided to protect the readoutlayer 3, the recording layer 4 and the auxiliary recording layer 5against oxidization, corrosion and damage.

The composition where the magnetic moment of the sublattice of therare-earth metal balances the magnetic moment of the sublattice of thetransition metal is called a compensating composition. The compositioncontaining an amount of the rare-earth metal which is greater than thatcontained in the compensating composition is hereinafter referred to asRE-rich. The composition containing an amount of the transition metalwhich is greater than that contained in the compensating composition iscalled TM-rich.

If the composition is RE-rich, the orientation of magnetization isaligned with the orientation of the magnetic moment of the sublattice ofthe rare-earth metal. Namely, the magnetization and the magnetic momentsof the sublattice of the rare-earth metal become parallel to each other.On the other hand, if the composition is TM-rich, the orientation ofmagnetization is aligned with the orientation of the magnetic moment ofthe sublattice of the transition metal. In other words, themagnetization and the magnetic moment of the sublattice of therare-earth metal become antiparallel to each other.

If the readout layer 3 is RE-rich and if the recording layer 4 and theauxiliary recording layer 5 are TM-rich, reproduction of information andlight-intensity modulation overwriting are performed through the processshown in FIG. 3. In FIG. 3, arrows indicate the orientation of themagnetic moment of the sublattice of the rare-earth metal, while openarrows indicate the direction of magnetization.

At room temperature, state (a) where the magnetic moment of thesublattice of the rare-earth metal of each of the readout layer 3, therecording layer 4 and the auxiliary recording layer 5 is directed upwardand state (b) where the sublattice magnetic moments of the rare-earthmetal of these layers are all directed downward are present. Themagnetization of the readout layer 3 is antiparallel to themagnetization of the recording layer 4 and of the auxiliary recordinglayer 5 at room temperature.

In state (a) all the sublattice magnetic moments of the transition metalare directed downward, while in state (b) all the sublattice magneticmoments of the transition metal are directed upward. Since theorientation of the magnetic moment of the sublattice of the transitionmetal is opposite to that of the rare-earth metal, the explanation ofthe orientation of the sublattice magnetic moment of the transitionmetal will be omitted.

When performing reproduction, the laser light 8 of a predetermined poweris projected onto the magneto-optical recording medium. When thetemperatures of the readout layer 3, the recording layer 4 and theauxiliary recording layer 5 are raised to T_(read) of FIG. 2, the statesof these layers change from (a) and (b) to (a1) and (b1). At T_(read),although the coercive force of the recording layer 4 is decreased, it isstill strong. Therefore, in states (a1) and (b1), the orientations ofmagnetization and the sublattice magnetic moments remain unchanged fromstates (a) and (b). Consequently, information on the recording layer 4is reproduced by reading the orientation of magnetization of the readoutlayer 3 using polar Kerr effect.

When performing overwriting by light-intensity modulation, the laserlight 8 of a first power which is greater than the power used forreproduction is projected onto the magneto-optical recording medium.When the temperatures of the readout layer 3, the recording layer 4 andthe auxiliary recording layer 5 are increased to T_(L) of FIG. 2, thestates of these layers change from (a) and (b) to (a2) and (b2) through(a1) and (b1). T_(L) is a temperature near the Curie temperature T_(c2)of the recording layer 4. Since the direction of magnetization of thereadout layer 3 and of the auxiliary recording layer 5 are aligned withthe direction of a uniform magnetic field H_(B) (downward in thisembodiment), the sublattice magnetic moment of the readout layer 3 andthat of the auxiliary recording layer 5 become antiparallel to eachother.

The exchange coupling force from the readout layer 3 causes the magneticmoment of the sublattice of the recording layer 4 to be directeddownward. The exchange coupling force from the auxiliary recording layer5 causes the magnetic moment of the sublattice of the recording layer 4to be directed upward. The magnetostatic coupling force produced by therecording magnetic filed H_(B) causes the recording layer 4 to havedownward magnetization. Since the laser light 8 is applied to theauxiliary recording layer 5 through the readout layer 3, (the averagetemperature T1 of the readout layer 3)>(the average temperature T2 ofthe auxiliary recording layer 5). Thus, the force to produce downwardmagnetization of the recording layer 4 becomes stronger than the forceto produce upward magnetization. Hence, in states (a2) and (b2), therecording layer 4 has downward magnetization.

When the projection of the laser light 8 is stopped, the temperature isdecreased and the coercive force of the recording layer 4 is rapidlyincreased. Consequently, the state of the recording layer 4 changes from(a2) and (b2) to (a) through (a1) while having downward magnetization.

Next the laser light 8 of the second power which is greater than thefirst power is projected onto the magneto-optical recording medium. Whenthe temperatures of the readout layer 3, the recording layer 4 and theauxiliary recording layer 5 are increased to T_(H) of FIG. 2, the statesof these layers change from (a) and (b) to (c) through (a1), (b1), (a2)and (b2). T_(H) is a temperature in the vicinity of the Curietemperature T_(C1) of the readout layer 3. The Curie temperature T_(C1)of the readout layer 3 is almost equal to the Curie temperature T_(C3)of the auxiliary recording layer 5.

In state (c), since T_(H) >T_(C2), the magnetization of the recordinglayer 4 becomes zero. Since the magnetization of the readout layer 3 andthe auxiliary recording layer 5 are aligned with the direction of theexternal uniform magnetic filed H_(B), the magnetic moment of thesublattice of the readout layer 3 becomes antiparallel to the magneticmoment of the sublattice of the auxiliary recording layer 5.

When the projection of the laser light 8 is stopped, the temperatures ofthese layers are decreased and their states change to (c2) at T_(L). Atthis time, since the direction of magnetization of the readout layer 3and of the auxiliary recording layer 5 are kept aligned with thedirection of the external uniform magnetic filed H_(B), the magneticmoment of the sublattice of the readout layer 3 becomes antiparallel tothe magnetic moment of the sublattice of the auxiliary recording layer5.

The exchange coupling force from the readout layer 3 causes the magneticmoment of the sublattice of the recording layer 4 to have the downwardorientation, while the exchange coupling force from the auxiliaryrecording layer 5 causes the magnetic moment of the sublattice of therecording layer 4 to have the upward orientation. The magnetostaticforce produced by the recording magnetic filed H_(B) causes the downwardmagnetization of the recording layer 4. In state (c), (the averagetemperature T1' of the readout layer 3)>(the average temperature T2' ofthe auxiliary recording layer 5), diffusion of heat in the direction ofthe thickness of the layers proceeds with a decrease in the temperaturesand the temperature differences in the direction of the thickness of thelayers are eliminated. Thus, T1' and T2' become equal to each other instate (c2), and the force to produce upward magnetization of therecording layer 4 becomes greater than the force to produce downwardmagnetization. Consequently, the recording layer 4 has upwardmagnetization in state (c2).

When the temperature is further decreased, the coercive force of therecording layer 4 is rapidly increased. As a result, the state of therecording layer 4 changes to (c1) at T_(READ) and to (b) at roomtemperature while keeping upward magnetization.

As described above, if the temperature of the recording medium isdecreased to room temperature after projecting the laser light 8 of thefirst power, the states of the readout layer 3, the recording layer 4and the auxiliary recording layer 5 change from (a) and (b) to (a). Onthe other hand, if the temperature of the recording medium is decreasedto room temperature after projecting the laser light 8 of the secondpower, the states of these layers change from (a) and (b) to (b). It isthus possible to perform overwriting by light-intensity modulation.

When the readout layer 3, the recording layer 4 and the auxiliaryrecording layer 5 are formed on the substrate 1 (see FIG. 4), exchangecoupling forces are produced between the layers 3 and 4 and between thelayers 4 and 5. Therefore, if the magnetization of the recording layer 4is finite (i.e., is not zero) or if the temperature of the recordinglayer 4 falls below T_(C2), the coercive force of the readout layer 3becomes greater than that of the readout layer 3 when formed alone (seeFIG. 2). Similarly, the coercive forces of the recording layer 4 and theauxiliary recording layer 5 become substantially equal to each other, orthe coercive force of the auxiliary recording layer 5 becomes slightlysmaller than that of the recording layer 4.

Moreover, when the readout layer 3, the recording layer 4 and theauxiliary recording layer 5 are formed on the substrate 1, the polarKerr rotation angle of the readout layer 3 shows abnormal hysteresischaracteristics at room temperature and T_(READ) (reading temperature)at which the coercive force of the recording layer 4 is strong as shownin FIG. 5. Meanwhile, the recording layer 4 and the auxiliary recordinglayer 5 show normal hysteresis characteristics of a TM-rich magneticsubstance.

The following description discusses a magneto-optical disk including thereadout layer 3, the recording layer 4, and the auxiliary recordinglayer 5 having magnetic properties of FIG. 2 as a first sample (#1-1) ofthe magneto-optical recording medium of this embodiment.

The substrate 1 is made of a disk-shaped glass with a diameter of 86 mm,an inner diameter of 15 mm and a thickness of 1.2 mm. Although it is notshown, lands and grooves are formed on a surface of the substrate 1 toproduce a guide track for guiding a light beam. The track is formed witha pitch of 1.6 μm, a groove width of 0.8 μm and a land width of 0.8 μm.

AlN with a thickness of 80 nm is formed as the transparent dielectriclayer 2 on a surface of the substrate 1 where the guide track is formed.

The readout layer 3, the recording layer 4 and the auxiliary layer 5having the magnetic properties of FIG. 2 are formed on the transparentdielectric layer 2.

For the readout layer 3, a thin film of rare-earth transition metalalloy made of RE-rich GdFeCo with a thickness of 50 nm is formed on thetransparent dielectric layer 2. The composition of GdFeCo is Gd₀.26(Fe₀.82 Co₀.18)₀.74, and the Curie temperature thereof is around 300° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of TM-rich DyFeCo with a thickness of 50 nm is formed on thereadout layer 3. The composition of DyFeCo is Dy₀.23 (Fe₀.78Co₀.22)₀.77, and the Curie temperature thereof is around 200° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed on the recording layer 4. The composition of GdFeCo is Gd₀.17(Fe₀.82 Co₀.18)₀.83, and the Curie temperature thereof is around 320° C.

AlN with a thickness of 20 nm is placed as a protective film 6 on theauxiliary recording layer 5.

A polyurethane acrylate series ultraviolet rays-hardening resin with athickness of 5 μm is placed as an overcoat film 7 on the protective film6.

The process of producing the magneto-optical disk is as follows.

The guide track on the surface of the glass substrate 1 is formed byreactive ion etching.

The transparent dielectric layer 2, the readout layer 3, the recordinglayer 4, the auxiliary recording layer 5 and the protective film 6 arerespectively formed by the sputtering method under vacuum in the samesputtering device. AlN for the transparent dielectric layer 2 and theprotective film 6 was formed in N₂ gas atmosphere by the reactivesputtering method in which the sputtering of Al target was carried out.The readout layer 3 and the recording layer 4 were formed by sputteringa so-called composite target produced by arranging Gd or Dy tips on aFeCo alloy target, or ternary alloy target of GdFeCo and DyFeCo using Argas.

The overcoat film 7 was formed by applying a polyurethane acrylateseries ultraviolet rays-hardening resin using a spin coating machine,and by hardening the resin by projecting ultraviolet light using anultraviolet light application device.

The magneto-optical disk thus manufactured is rotated at a linearvelocity of 10 m/s, and recording is performed by modulating the laserpower at a frequency of 2.5 MHz while applying a uniform magnetic fieldH_(B) of 25 kA/m. Here, the first laser power was set at 6 mW, and thesecond laser power was set at 10 mW. As a result, a magnetic domainwhose magnetization is reversed every 2 μm was formed on the recordinglayer 4.

Next, the power of the laser light 8 was set at 2 mW, and thereproduction of information was carried out. As a result, amagneto-optical signal of 2.5 MHz corresponding to the reversal magneticdomain was obtained from the readout layer 3.

Light-intensity modulation overwriting was performed on the reversalmagnetic domain by modulating the laser power at a frequency of 5 MHz.As a result, the reversal magnetic domain disappears, and a reversalmagnetic domain whose magnetization is reversed every 1 μm was formed onthe recording layer 4.

Then, the power of the laser light 8 was set at 2 mW, and reproductionof information was carried out. As a result, a magneto-optical signal of5 MHz corresponding to the reversal magnetic domain is obtained from thereadout layer 3.

According to the results of experiments, the feasibility of goodlight-intensity modulation overwriting was confirmed.

In the above explanation about the light-intensity modulationoverwriting, the magneto-optical disk having the RE-rich readout layer3, the TM-rich recording layer 4 and the TM-rich auxiliary recordinglayer 5 was discussed. However, it is also possible to use amagneto-optical disk having a TM-rich readout layer 3, a TM-richrecording layer 4 and a RE-rich auxiliary recording layer 5 whenperforming the reproduction of information and the light-intensitymodulation, overwriting through the process shown in FIG. 6. Namely, thematerials of the readout layer 3 and the auxiliary recording layer 5 areinterchangeable.

It is also possible to perform the reproduction of information and thelight-intensity modulation overwriting through the process shown in FIG.8 using a magneto-optical disk having the RE-rich readout layer 3, theRE-rich recording layer 4 and the TM-rich auxiliary recording layer 5whose coercive force individually shows the temperature dependence ofFIG. 7.

Since this magneto-optical recording medium has the RE-rich recordinglayer 4, the sublattice magnetic moment of the rare-earth metal of therecording layer 4 is parallel to the magnetization thereof. Therefore,the direction of the magnetostatic coupling force exerted on therecording layer 4 by the uniform magnetic field H_(B) is changed. Atemperature distribution is observed in the direction of film thicknessat T_(L) and overwriting by light intensity modulation becomes availableas like on the above-mentioned magneto-optical recording medium.

The following description discusses a magneto-optical disk including thereadout layer 3, the recording layer 4, and the auxiliary recordinglayer 5 having magnetic properties shown in FIG. 7 as a second sample(#1-2) of the magneto-optical recording medium of this embodiment.

For the readout layer 3, a thin film of rare-earth transition metalalloy made of RE-rich GdFeCo with a thickness of 50 nm is formed. Thecomposition of GdFeCo is Gd₀.26 (Fe₀.82 Co₀.18)₀.74, and the Curietemperature thereof is around 300° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of RE-rich DyFeCo with a thickness of 50 nm is-formed. Thecomposition of DyFeCo is Dy₀.35 (Fe₀.78 Co₀.22)₀.65, and the Curietemperature thereof is around 170° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed. The composition of GdFeCo is Gd₀.17 (Fe₀.82 Co₀.18)₀.83, andthe Curie temperature thereof is around 320° C.

Except for these changes, the sample (#1-2) has the same structure asthat of the sample (#1-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed.

In the above explanation about the light-intensity modulationoverwriting, the magneto-optical disk having the RE-rich readout layer3, the RE-rich recording layer 4 and the TM-rich auxiliary recordinglayer 5 was discussed. However, it is also possible to use amagneto-optical disk having a TM-rich readout layer 3, the RE-richrecording layer 4 and a RE-rich auxiliary recording layer 5 whenperforming the reproduction of information and the light-intensitymodulation overwriting. Namely, the materials of the readout layer 3 andthe auxiliary recording layer 5 are interchangeable.

It is also possible to perform the reproduction of information and thelight-intensity modulation overwriting through the process shown in FIG.10 using a magneto-optical disk having the RE-rich readout layer 3, arecording layer 4 whose compensation temperature is T_(COMP) and theTM-rich auxiliary recording layer 5, the coercive force of these layersindividually showing the temperature dependence of FIG. 9.

With this magneto-optical disk, since the recording layer 4 has acompensation temperature T_(COMP) between T_(READ) and T_(L), themagnetization of the recording layer 4 is reversed at temperaturesaround the compensation temperature T_(COMP). However, states (a2), (b2)and (c2) at T_(L) are equal to those of the above-mentionedmagneto-optical recording medium. It is therefore possible to performthe light-intensity modulation overwriting in the above-mentionedmanner.

Moreover, when the temperature of the recording layer 4 is decreasedfrom T_(C2), the coercive force rapidly increases as the temperaturecomes closer to the compensation temperature T_(COMP). It is thuspossible to perform more stable light-intensity modulation overwritingwith the magneto-optical disk of this composition than with theabove-mentioned magneto-optical recording medium.

The following description discusses a magneto-optical disk including thereadout layer 3, the recording layer 4, and the auxiliary recordinglayer 5 having magnetic properties shown in FIG. 9 as a third sample(#1-3) of the magneto-optical recording medium of this embodiment.

For the readout layer 3, a thin film of rare-earth transition metalalloy made of RE-rich GdFeCo with a thickness of 50 nm was formed. Thecomposition of GdFeCo is Gd₀.26 (Fe₀.82 Co₀.18)₀.74, and the Curietemperature thereof is around 300° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of DyFeCo with a thickness of 50 nm and the compensationtemperature T_(COMP) is formed. The composition of DyFeCo is Dy₀.25(Fe₀.78 Co₀.22)₀.75, and the Curie temperature thereof is around 190° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed. The composition of GdFeCo is Gd₀.17 (Fe₀.82 Co₀.18)₀.83, andthe Curie temperature thereof is around 320° C.

Except for these changes, the sample (#1-3) has the same structure asthat of the sample (#1-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed.

In the above explanation about the light-intensity modulationoverwriting, the magneto-optical disk having the RE-rich readout layer3, the recording layer 4 having the compensation temperature T_(COMP)and the TM-rich auxiliary recording layer 5 was discussed. However, itis also possible to use a magneto-optical disk having the TM-richreadout layer 3, the recording layer 4 having the compensationtemperature T_(COMP) and the RE-rich auxiliary recording layer 5 whenperforming the reproduction of information and the light-intensitymodulation overwriting. Namely, the materials of the readout layer 3 andthe auxiliary recording layer 5 are interchangeable.

The following description discusses the second embodiment of the presentinvention with reference to FIGS. 11 to 19. The members having the samefunction as in the above-mentioned embodiment will be designated by thesame code and their description will be omitted.

As illustrated in FIG. 11, a magneto-optical recording medium of thisembodiment is produced by forming the transparent dielectric layer 2, areadout layer 3a, the recording layer 4, the auxiliary recording layer5, the protective film 6 and the overcoat film 7 in this order on thesubstrate 1. Recording and reproduction are performed by focusing laserlight 8 on the readout layer 3a with a converging lens 9.

The readout layer 3a of this embodiment differs from that of theabove-mentioned embodiment on the following point. The readout layer 3aof this embodiment has in-plane magnetization at room temperaturebecause in-plane magnetic anisotropy is larger than perpendicularmagnetic anisotropy. With an increase of temperature, the perpendicularmagnetic anisotropy becomes larger than the in-plane magnetic anisotropyand the readout layer 3a tends to have perpendicular magnetization.

An amorphous film formed by an alloy of rare-earth metal and transitionmetal is a ferrimagnetic material. The temperature dependence of thesublattice magnetic moment of the rare-earth metal and that of thetransition metal are different from each other, and the latter becomesgreater than the former at high temperatures. Then, in order to havein-plane magnetization at room temperature, RE-rich material is used forthe readout layer 3a. When the temperature of the readout layer 3a isincreased with the application of laser light 8, the sublattice magneticmoment of the rare-earth metal and that of the transition metal balance.This causes the readout layer 3a to have perpendicular magnetization.The temperature at which transition from in-plane magnetization toperpendicular magnetization occurs is referred to as T_(P).

FIG. 12 shows the temperature dependence of coercive forces of thereadout layer 3a, the recording layer 4 and the auxiliary recordinglayer 5. FIG. 14 shows the temperature dependence of coercive forces ofthese layers when they are formed on the substrate 1.

If the recording layer 4 and the auxiliary recording layer 5 areTM-rich, reproduction of information and light-intensity modulationoverwriting are performed through the process shown in FIG. 13.

In states (a) and (b) at room temperature, the orientations ofmagnetization and the sublattice magnetic moment of the readout layer 3aare different from those of the above-mentioned embodiment (see FIG. 3).However, in states (a1), (a2), (b1), (b2), (c1) and (c2), they are thesame as those of the above-mentioned embodiment. Like theabove-mentioned embodiment, if the temperature of the recording mediumis decreased to room temperature after projecting the laser light 8 ofthe first power, the states of the readout layer 3a change from (a) and(b) to (a). On the other hand, if the temperature of the recordingmedium is decreased to room temperature after projecting the laser light8 of the second power, the states of the readout layers 3a change from(a) and (b) to (b). It is thus possible to perform light-intensitymodulation overwriting.

When the readout layer 3a, the recording layer 4 and the auxiliaryrecording layer 5 are formed on the substrate 1 (see FIG. 14), anexchange coupling force is produced between the layers 3a and 4 andbetween layers 4 and 5. Therefore, if the magnetization of the recordinglayer 4 is finite (i.e., is not zero) or if the temperature of therecording layer 4 falls below T_(C2), the coercive force of the readoutlayer 3a becomes greater than that of the readout layer 3a when usedalone (see FIG. 12). Similarly, the coercive forces of the recordinglayer 4 and the auxiliary recording layer 5 become substantially equalto each other, or the coercive force of the auxiliary recording layer 5becomes slightly smaller than that of the recording layer 4.

Moreover, when the readout layer 3a, the recording layer 4 and theauxiliary recording layer 5 are formed on the substrate 1, the readoutlayer 3a shows abnormal hysteresis characteristics at T_(READ) (readingtemperature) at which the coercive force of the recording layer 4 isstrong as shown in FIG. 15. Meanwhile, the recording layer 4 and theauxiliary recording layer 5 show normal hysteresis characteristics of aTM-rich magnetic substance. The temperature T_(P) at which the readoutlayer 3a has perpendicular magnetization is lowered by the exchangecoupling. It is therefore desirable to determine the composition of thereadout layer 3a so that T_(P) comes between the room temperature andT_(READ) when the readout layer 3a, the recording layer 4 and theauxiliary recording layer 5 are formed on the substrate 1.

The following description discusses the reproduction of information.

When the laser light 8 (see FIG. 11) which has passed through thesubstrate 1 is focused into a light spot on the readout layer 3a by theconverging lens 9, the center part of a portion of the readout layer 3aexposed to the laser light 8 has the highest temperature. Since thelaser light 8 is converged just before the limit of diffraction, thedistribution of light intensity of the laser light 8 becomes Gaussian.Thus, the temperature distribution of the portion exposed to the laserlight 8 also becomes Gaussian.

If the intensity of the laser light 8 is determined so that the centerpart of the portion exposed to the laser light 8 has a temperature notlower than T_(READ) and that portions around the center part havetemperatures not higher than T_(P), only portions of the readout layer3a having temperatures not lower than T_(P) have transition fromin-plane magnetization to perpendicular magnetization and portionshaving temperatures not higher than T_(P) maintain in-planemagnetization. The direction of magnetization of the portions of readoutlayer 3a having perpendicular magnetization is aligned with that of therecording layer 4 due to exchange coupling forces between the readoutlayer 3a and the recording layer 4. When the laser light 8 is projectedperpendicularly to the readout layer 3a, the polar Kerr effect isproduced only on the portions having perpendicular magnetization, andtherefore the effect is not produced in the portions having in-planemagnetization. It is therefore possible to reproduce only theinformation from the portions having temperatures not lower than T_(P)with reflected light from the readout layer 3a.

When the laser light 8 and the magneto-optical recording medium aremoved with respect to each other, the temperatures of the portionshaving temperatures not lower than T_(P) are decreased and transitionfrom perpendicular magnetization to in-plane magnetization occur.Consequently, the polar Kerr effect is not produced in the portions.This prevents the mixing of the signal from the portion exposed to thelaser light 8 and signals from adjacent recording bits.

As described above, with the magneto-optical recording medium of thisembodiment, it is possible to reproduce a recording bit smaller than thesize of the light spot on the readout layer 3a and to prevent the mixingof the signal from the portion exposed to the laser light 8 and thesignals from adjacent recording bits. As a result, the recording densityis significantly improved.

The following description discusses a magneto-optical disk including thereadout layer 3a, the recording layer 4 and the auxiliary recordinglayer 5 having magnetic properties of FIG. 12 as a first sample (#2-1)of the magneto-optical recording medium of this embodiment.

For the readout layer 3a, a thin film of rare-earth transition metalalloy made of RE-rich GdFeCo with a thickness of 50 nm is formed. Thecomposition of GdFeCo is Gd₀.29 (Fe₀.82 Co₀.18)₀.71, and the Curietemperature thereof is around 280° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of TM-rich DyFeCo with a thickness of 50 nm is formed. Thecomposition of DyFeCo is Dy₀.23 (Fe₀.78 Co₀.22)₀.77, and the Curietemperature thereof is around 200° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed on the recording layer 4. The composition of GdFeCo is Gd₀.17(Fe₀.82 Co₀.18)₀.83, and the Curie temperature thereof is around 320° C.

Except for these changes, this sample has the same structure as that ofthe first sample (#1-1) of the above-mentioned embodiment.

When the readout layer 3a, the recording layer 4 and the auxiliaryrecording layer 5 are laminated, the readout layer 3a substantially hasin-plane magnetization at room temperature, and transition from in-planemagnetization to perpendicular magnetization occurs at temperatures 100°to 125° C.

The magneto-optical disk was rotated at a linear velocity of 10 m/s, andrecording was performed by modulating the laser power at a frequency of5 MHz while applying a uniform magnetic field H_(B) of 25 kA/m. Here,the first laser power was set at 6 mW, and the second laser power wasset at 10 mW. As a result, a magnetic domain whose magnetization isreversed every 1 μm was formed on the recording layer 4.

Next, the power of the laser light 8 was set at 2 mW, and thereproduction of information was carried out. As a result, amagneto-optical signal of 5 MHz corresponding to the reversal magneticdomain was obtained from the readout layer 3a.

Light-intensity modulation overwriting was performed on the reversalmagnetic domain by modulating the laser power at a frequency of 10 MHz.As a result, the reversal magnetic domain disappears, and a reversalmagnetic domain whose magnetization is reversed every 0.5 μm was formedon the recording layer 4.

Then, the power of the laser light 8 was set at 2 mW, and reproductionof information was carried out. As a result, a magneto-optical signal of10 MHz corresponding to the reversal magnetic domain was obtained fromthe readout layer 3a.

The signal intensity of the 10 MHz magneto-optical signal issubstantially equal to that of the 5 MHz magneto-optical signal. Thisindicates that the information was reproduced from a portion of therecording layer 4 corresponding to a portion of the readout layer 3ahaving perpendicular magnetization.

According to the results of experiments, the feasibility of goodlight-intensity modulation overwriting was confirmed.

In the above explanation about the light-intensity modulationoverwriting and reproduction, the magneto-optical disk having theTM-rich recording layer 4 and the TM-rich auxiliary recording layer 5was discussed. However, it is also possible to use a magneto-opticaldisk having the RE-rich recording layer 4 instead of the TM richrecording layer 4 when performing the reproduction of information andthe light-intensity modulation overwriting through the process shown inFIG. 17, wherein the coercive forces of the readout layer 3a, therecording layer 4 and the auxiliary recording layer 5 individually showthe temperature dependence of FIG. 16.

In this case, since the magneto-optical recording medium has the RE-richrecording layer 4, the sublattice magnetic moment of the rare-earthmetal of the recording layer 4 is parallel to the magnetization.Therefore, the direction of magnetostatic coupling force exerted on therecording layer 4 by the uniform magnetic field H_(B) is changed.However, by producing temperature distribution in the direction of filmthickness at T_(L), the light-intensity modulation overwriting isperformed in the same manner as that performed using the above-mentionedmagneto-optical recording medium. Moreover, since the coercive force israpidly increased when the temperature of the recording layer 4 fallsbelow T_(C2), the light-intensity modulation overwriting using such amagneto-optical recording medium is more stable than that performed withthe above-mentioned magneto-optical recording medium. As forreproduction, like the above-mentioned magneto-optical recording medium,it is possible to reproduce a recording bit smaller than the size of thelight spot on the readout layer 3a and to prevent the mixing of thesignal from the portion exposed to the laser light 8 and the signalsfrom adjacent recording bits. As a result, the recording density issignificantly improved.

The following description discusses a magneto-optical disk including thereadout layer 3a, the recording layer 4, and the auxiliary recordinglayer 5 having magnetic properties of FIG. 16 as a second sample (#2-2)of the magneto-optical recording medium of this embodiment.

For the readout layer 3a, a thin film of rare-earth transition metalalloy made of RE-rich GdFeCo with a thickness of 50 nm is formed. Thecomposition of GdFeCo is Gd₀.29 (Fe₀.82 Co₀.18)₀.71, and the Curietemperature thereof is around 280° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of RE-rich DyFeCo with a thickness of 50 nm is formed. Thecomposition of DyFeCo is Dy₀.35 (Fe₀.78 Co₀.22)₀.65, and the Curietemperature thereof is around 170° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed on the recording layer 4. The composition of GdFeCo is Gd₀.17(Fe₀.82 Co₀.18)₀.83, and the Curie temperature thereof is around 320° C.

When the readout layer 3a, the recording layer 4 and the auxiliaryrecording layer 5 are laminated, the readout layer 3a substantially hasin-plane magnetization at room temperature, and transition from in-planemagnetization to perpendicular magnetization occurs at temperatures 100°to 125° C.

Except for these changes, this sample has the same structure as that ofthe sample (#2-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed.

It is also possible to perform the reproduction of information and thelight-intensity modulation overwriting through the process shown in FIG.19 using a magneto-optical recording medium including the readout layer3, the recording layer 4 having the compensation temperature T_(COMP)and the auxiliary recording layer 5, the coercive forces of these layersindividually showing the temperature dependence of FIG. 18.

In this case, since the recording layer 4 has the compensationtemperature T_(COMP) between T_(READ) and T_(L), the magnetization ofthe recording layer 4 is reversed at temperatures around thecompensation temperature T_(COMP). However, by producing temperaturedistribution in the direction of film thickness at T_(L), thelight-intensity modulation overwriting is performed in the same manneras that performed using the above-mentioned magneto-optical recordingmedium. Moreover, since the coercive force is rapidly increased when thetemperature of the recording layer 4 falls below T_(C2), thelight-intensity modulation overwriting using such a magneto-opticalrecording medium is more stable than that performed with theabove-mentioned magneto-optical recording medium. As for reproduction,like the above-mentioned magneto-optical recording medium, it ispossible to reproduce a recording bit smaller than the size of the lightspot on the readout layer 3a and to prevent the mixing of the signalfrom the portion exposed to the laser light 8 and the signals fromadjacent recording bits. As a result, the recording density issignificantly improved.

The following description discusses a magneto-optical disk including thereadout layer 3a, the recording layer 4, and the auxiliary recordinglayer 5 having magnetic properties of FIG. 18 as a third sample (#2-3)of the magneto-optical recording medium of this embodiment. For thereadout layer 3a, a thin film of rare-earth transition metal alloy madeof RE-rich GdFeCo with a thickness of 50 nm is formed. The compositionof GdFeCo is Gd₀.29 (Fe₀.82 Co₀.18)₀.71, and the Curie temperaturethereof is around 280° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of DyFeCo with a thickness of 50 nm and the compensationtemperature T_(COMP) is formed. The composition of DyFeCo is Dy₀.25(Fe₀.78 Co₀.22)₀.75, and the Curie temperature thereof is around 190° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of TM-rich GdFeCo with a thickness of 50 nmis formed. The composition of GdFeCo is Gd₀.17 (Fe₀.82 Co₀.18)₀.83, andthe Curie temperature thereof is around 320° C.

When the readout layer 3a, the recording layer 4 and the auxiliaryrecording layer 5 are laminated, the readout layer 3a substantially hasin-plane magnetization at room temperature, and transition from in-planemagnetization to perpendicular magnetization occurs at temperatures 100°to 125° C.

Except for these changes, this sample has the same structure as that ofthe sample (#2-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults,.the feasibility of satisfactory light-intensity modulationoverwriting and and reproducing high dense information was confirmed.

The following description discusses a third embodiment of the presentinvention with reference to FIG. 20. The members having the samefunction as in the above-mentioned embodiment will be designated by thesame code and their description will be omitted.

As illustrated in FIG. 20, a magneto-optical recording medium of thisembodiment is produced by forming the transparent dielectric layer 2,the readout layer 3, an intermediate layer 10, the recording layer 4, anintermediate layer 11, the auxiliary recording layer 5, the protectivefilm 6 and the overcoat film 7 in this order on the substrate 1.

The inclusion of the intermediate layer 10 makes it possible to controlthe exchange force between the readout layer 3 and the recording layer4. With this structure, a magneto-optical recording medium allowing thelight-intensity modulation overwriting is easily achieved.

The inclusion of the intermediate layer 11 makes it possible to controlthe exchange force between the recording layer 4 and the auxiliaryrecording layer 5. With this structure, a magneto-optical recordingmedium allowing the light-intensity modulation overwriting is easilyachieved.

The following description discusses a magneto-optical disk including theintermediate layer 10 between the readout layer 3 and the recordinglayer 4 as a first sample (#3-1) of the magneto-optical recording mediumof this embodiment.

For the intermediate layer 10, FeCo as a film having in-planemagnetization is formed with a thickness of 2 nm. The composition ofFeCo is Fe₀.8 Co₀.2.

Except for the intermediate layer 10, this sample has the same structureas that of the first sample (#1-1) of the first embodiment.

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layer 10 is included, the optimumvalue of the recording magnetic field H_(B) became 30 kA/m.

Next, a magneto-optical disk including the intermediate layer 11 betweenthe recording layer 4 and the auxiliary recording layer 5 is explainedas a second sample (#3-2) of the magneto-optical recording medium ofthis embodiment.

For the intermediate layer 11, FeCo as a film having in-planemagnetization is formed with a thickness of 2 nm. The composition ofFeCo is Fe₀.8 Co₀.2.

Except for the intermediate layer 11, this sample has the same structureas that of the above-mentioned first sample (#1-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layer 11 is included, the optimumvalue of the recording magnetic filed H_(B) became 20 kA/m.

Next, a magneto-optical disk including the intermediate layers 10 and 11is explained as a third sample (#3-3) of the magneto-optical recordingmedium of this embodiment.

For the intermediate layers 10 and 11, FeCo as a film having in-planemagnetization is formed with a thickness of 2 nm. The composition ofFeCo is Fe₀.8 Co₀.2.

Except for the intermediate layers 10 and 11, this sample has the samestructure as that of the above-mentioned first sample (#1-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layers 10 and 11 were included,the optimum value of the recording magnetic filed H_(B) became 25 kA/m.

The following description discusses a fourth embodiment of the presentinvention with reference to FIG. 21. The members having the samefunction as in the above-mentioned embodiment will be designated by thesame code and their description will be omitted.

As illustrated in FIG. 21, a magneto-optical recording medium of thisembodiment was produced by forming the transparent dielectric layer 2,the readout layer 3a, an intermediate layer 10, the recording layer 4,an intermediate layer 11, the auxiliary recording layer 5, theprotective film 6 and the overcoat film 7 in this order on thesubstrate 1. The intermediate layer 10 made of a film having in-planemagnetization of the second embodiment was formed between the readoutlayer 3a and the recording layer 4, and the intermediate layer 11 madeof a film having in-plane magnetization film was formed between therecording layer 4 and the auxiliary recording layer 5.

The inclusion of the intermediate layer 10 makes it possible to controlthe exchange coupling force between the readout layer 3a and therecording layer 4. With this structure, a magneto-optical recordingmedium allowing the light-intensity modulation overwriting is easilyachieved.

Also, the inclusion of the intermediate layer 11 makes it possible tocontrol the exchange coupling force between the recording layer 4 andthe auxiliary recording layer 5. With this structure, a magneto-opticalrecording medium allowing the light-intensity modulation overwriting iseasily achieved.

The following description discusses a magneto-optical disk including theintermediate layer 10 between the readout layer 3a and -the recordinglayer 4 as a first sample (#4-1) of the magneto-optical recording mediumof this embodiment.

For the intermediate layer 10, FeCo as a film having in-planemagnetization film was formed with a thickness of 2 nm. The compositionof FeCo is Fe₀.8 Co₀.2.

Except for the intermediate layer 10, this sample has the same structureas that of the first sample (#2-1) of the second embodiment.

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layer 10 was included, the optimumvalue of the recording magnetic filed H_(B) became 30 kA/m.

Next, a magneto-optical disk including the intermediate layer 11 betweenthe recording layer 4 and the auxiliary recording layer 5 is explainedas a second sample (#4-2) of the magneto-optical recording medium ofthis embodiment.

For the intermediate layer 11, FeCo as a film having in-planemagnetization was formed with a thickness of 2 nm. The composition ofFeCo is Fe₀.8 Co₀.2.

Except for the intermediate layer 11, this sample has the same structureas that of the above-mentioned sample (#2-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layer 11 was included, the optimumvalue of the recording magnetic filed H_(B) became 20 kA/m.

Next, a magneto-optical disk including the intermediate layers 10 and 11is explained as a third sample (#4-3) of the magneto-optical recordingmedium of this embodiment.

For the intermediate layers 10 and 11, FeCo as a film having in-planemagnetization was formed with a thickness of 2 nm. The composition ofFeCo is Fe₀.8 Co₀.2.

Except for the intermediate layers 10 and 11, this sample has the samestructure as that of the above-mentioned sample (#2-1).

Recording and reproduction tests were conducted using themagneto-optical disk in the above-mentioned manner. According to theresults, the feasibility of good light-intensity modulation overwritingwas confirmed. Since the intermediate layers 10 and 11 were included,the optimum value of the recording magnetic filed H_(B) became 25 kA/m.

The following description discusses the components of themagneto-optical recording media of the first to fourth embodiments.

The composition of GdFeCo of the readout layer 3 is not restricted toGd₀.26 (Fe₀.82 Co₀.18)₀.74. Similarly, the composition of the readoutlayer 3a is not restricted to Gd₀.29 (Fe₀.82 Co₀.18)₀.71. The conditionsto be satisfied by the readout layers 3 and 3a are that the sublatticemagnetic moments of the readout layers 3 and 3a become antiparallel tothe sublattice magnetic moment of the auxiliary recording layer 5 in thevicinity of the Curie temperature T_(C2) of the recording layer 4, thereadout layer 3 has perpendicular magnetization up to the Curietemperature T_(C1) and that the readout layer 3a has in-planemagnetization at room temperature and perpendicular magnetization attemperatures above the room temperature.

It is not necessary that the readout layer 3a has perfect in-planemagnetization at room temperature nor shows transition from in-planemagnetization to perfect perpendicular magnetization at temperaturesabove room temperature. The requirement for the readout layer 3a is thatthe direction of magnetization at room temperature differs from thedirection of magnetization at T_(READ).

As for the rare-earth transition metal alloy, by varying the ratio ofthe rare-earth metal to the transition metal, the-compensationtemperature at which the magnetization of the rare-earth metal and thatof the transition metal balance is varied. Since GdFeCo is a materialseries which has perpendicular magnetization at temperatures in thevicinity of the compensation temperature, a material satisfying theabove-mentioned conditions is obtained by changing the ratio of Gd toFeCo.

FIG. 22 shows experimental results of compensation temperature and Curietemperature with a variable X in Gd_(X) (Fe₀.82 Co₀.18)_(1-X), i.e.,when the composition of Gd was varied.

It is found that a material satisfying the conditions for the readoutlayer 3 is obtained by setting 0.20<X<0.27. Also, a material satisfyingthe conditions for the readout layer 3a is obtained by setting0.27≦X<0.32.

The range of X mentioned is effective only when a TM-rich material isused as the auxiliary recording layer 5 and Dy₀.23 (Fe₀.82 Co₀.18)₀.77having a film thickness of 50 nm is used as the recording layer 4. Themagnetic properties of the recording layer 3 or 3a are changed by themagnetic properties of the recording layer 4. It is therefore desirableto determine the material of the readout layer 3 or 3a by taking accountof the recording layer 4.

As for the readout layer 3 or 3a, it is possible to use an amorphousfilm made of an alloy of rare-earth transition metal such as GdFe, GdCo,GdTbFeCo, GdDyFeCo, NdGdFe, NdGdCo, NdGdTbFeCo and NdGdDyFeCo as well asGdFeCo.

Additionally, when the wavelength of the semiconductor laser as a lightsource of an optical pickup becomes less than 780 nm, a material whichhas a large Kerr polar rotation angle at the wavelength is also suitablefor the readout layer 3 or 3a.

As explained earlier, in the magneto-optical recording medium such asthe magneto-optical disk, the recording density is limited by the sizeof the light spot which is determined by the wavelength of the laserlight and the aperture of the converging lens 9. Namely, the recordingdensity on the magneto-optical disk is improved by using a semiconductorlaser with a shorter wavelength. At present, the semiconductor laserwith a wavelength of 670 nm to 680 nm has been in practical use, and SHGlaser with a wavelength equal to or below 400 nm has been earnestlystudied.

The Kerr polar rotation angle of the rare-earth transition metal alloyhas a wavelength dependence. In general, as the wavelength becomesshorter, the Kerr polar rotation angle becomes smaller. Therefore, withthe use of the film which has a large Kerr polar rotation angle at ashort wavelength, the signal intensity is increased, thereby achieving ahigh quality reproduced signal.

By adding a very small amount of at least one element selected from thegroup consisting of Nd, Pt, Pr and Pd to the above material for thereadout layer 3 or 3a, the greater Kerr polar rotation angle is achievedat a short wavelength while substantially maintaining the propertiesrequired for the readout layer 3 or 3a. It is thus possible to provide amagneto-optical recording medium which permits a high quality reproducedsignal even when the semiconductor laser with a short wavelength isused.

Moreover, by adding a very small amount of at least one element selectedfrom the group consisting of Cr, V, Nb, Mn, Be, and Ni to the abovematerial for the readout layer 3 or 3a, the resistance of the readoutlayer 3 or 3a to environmental conditions is improved. It is thuspossible to prevent the properties of the readout layer 3 or 3a fromdeteriorating by protecting it against oxidization caused by moistureand oxygen and to provide a magneto-optical recording medium havingprominent reliability for a long time.

In the above-mentioned embodiments, although the recording layer 3 or 3awas formed with a film thickness of 50 nm, the film thickness can bevaried.

In order to produce exchange coupling forces between the readout layer 3and the recording layer 4 during recording, it is desirable to producethe readout layer 3 having a thickness not smaller than 10 nm.

Additionally, in order to prevent the laser light 8 from passing throughthe readout layer 3a and reaching the recording layer 4 duringreproduction, it is desirable to arrange the film thickness of thereadout layer 3a to be not smaller than 20 nm and more preferably notsmaller than 50 nm. On the other hand, in order to facilitatetransferring of information from the recording layer 4 to the readoutlayer 3a, it is desirable to arrange the film thickness of the readoutlayer 3a to be not larger than 100 nm.

A material used for the recording layer 4 is needed to haveperpendicular magnetization in a temperature range from room temperatureto the Curie temperature TC₂. As for the Curie temperature, T_(C2)suitable for recording is between 150° C. and 250° C. Materials suitablefor the recording layer 4 are DyFeCo, TbFeCo, GdTbFe, NdDyFeCo, GdDyFeCoand GdTbFeCo.

Furthermore, by adding to the material for the recording layer 4 a verysmall amount of at least one element selected from the group consistingof Cr, V, Nb, Mn, Be and Ni, the long-time reliability of the recordinglayer 4 is improved. Although the film thickness of the recording layer4 is determined by taking account of the material, composition and filmthickness of the readout layer 3 or 3a, it is desirable to set the filmthickness between about 20 nm and 100 nm.

Although the composition of GdFeCo of the auxiliary recording layer 5 isnot restricted to Gd₀.17 (Fe₀.82 Co₀.18)₀.83, it is needed to bedetermined such that the sublattice magnetic moment of the auxiliaryrecording layer 5 becomes antiparallel to the sublattice magneticmoments of the readout layers 3 and 3a at temperatures in the vicinityof the Curie temperature T_(C2) of the recording layer 4. If the ratioof the rare-earth and the transition metal of the alloy of rare-earthtransition metal is changed, the compensation temperature at which themagnetization of the rare-earth and that of the transition metal balanceis varied. Since GdFeCo is a material series having perpendicularmagnetization near the compensation temperature, a material satisfyingthe above-mentioned requirements is obtained by changing the ratio of Gdto FeCo.

FIG. 22 shows the results of an experiment which was conducted toexamine the compensation temperature and the Curie temperature with avariable X in Gd_(X) (Fe₀.82 Co₀.18)_(1-X), i.e., when the compositionof Gd was varied.

When the RE-rich readout layer 3 or 3a is formed by a RE-rich material,the conditions for the auxiliary recording layer 5 are satisfied bysetting X within a range 0.10<X<0.20.

For the auxiliary recording layer 5, it is possible to use an amorphousfilm made of an alloy of rare-earth transition metal such as GdFe, GdCo,GdTbFeCo, GdDyFeCo, NdGdFe, NdGdCo, NdGdTbFeCo and NdGdDyFeCo as well asGdFeCo.

By adding a very small amount of at least one element selected from thegroup consisting of Cr, V, Nb, Mn, Be and Ni to the above material forthe auxiliary recording layer 5, the resistance of the auxiliaryrecording 5 to environmental conditions is improved. It is thus possibleto prevent the properties of the auxiliary recording layer 5 fromdeteriorating by protecting it against oxidization caused by moistureand oxygen and to provide a magneto-optical recording medium havinglong-time reliability.

In the above-mentioned embodiments, although the auxiliary recording 5was formed with a film thickness of 50 nm, the film thickness can bevaried. In order to produce exchange coupling forces between theauxiliary recording layer 5 and the recording layer 4 during recording,it is desirable to produce the auxiliary recording layer 5 having athickness not smaller than 10 nm.

Additionally, the film thickness of AlN of the transparent dielectriclayer 2 is not restricted to 80 nm.

The film thickness of the transparent dielectric layer 2 is determinedby taking account of the enhancement of Kerr effect which increases thepolar Kerr rotation angle using interference of light from the readoutlayer 3 when reproducing information from the magneto-optical disk.During reproduction, in order to improve the signal quality (C/N) asmuch as possible, it is necessary to increase the polar Kerr rotationangle. Therefore, the film thickness of the transparent dielectric layer2 is set to achieve the maximum polar Kerr rotation angle.

The film thickness is varied depending on the wavelength of thereproducing light and the refractive index of the transparent dielectriclayer 2. In this embodiment, AlN whose refractive index is 2.0 is usedwith respect to the reproducing light of a wavelength of 780 nm. Thus,if the film thickness of AlN of the transparent dielectric layer 2 issubstantially set between 30 nm and 120 nm, the Kerr effect is enhanced.A more preferable range of the film thickness of AlN of the transparentdielectric layer 2 is between 70 nm and 100 nm. Namely, if the filmthickness of AlN is within this range, the polar Kerr rotation anglebecomes almost maximum.

In the above explanation, the reproducing light with a wavelength of 780nm is used. When reproducing light with a wavelength of 400 nm, forexample, which is substantially a half of the above-mentioned wavelength780 nm is used, the thickness of the transparent dielectric layer 2 ispreferably set a half of the film thickness which is used with thereproducing light having a wavelength of 780 nm.

Additionally, when the refractive index of the transparent dielectriclayer 2 changes depending on a material used in the transparentdielectric layer 2 or the method used in manufacturing the transparentdielectric layer 2, the thickness of the transparent dielectric layer 2is adjusted so as to have a uniform value (=optical path length) whichis obtained by multiplying the refractive index by the film thickness.

In this embodiment, 160 nm was obtained as the optical path length ofthe transparent dielectric layer 2 by multiplying 2 (the refractiveindex) by 80 nm (the film thickness). When the refractive index of AlNchanges from 2 to 2.5, the film thickness is preferably set at 160nm/2.5=64 nm.

As can be seen from the above explanation, the larger the refractiveindex of the transparent dielectric layer 2 becomes, the smaller thefilm thickness of the transparent dielectric layer 2 is. Also, the polarKerr rotation angle is enhanced with an increase in the refractiveindex.

The refractive index of AlN changes with a change in the ratio of Ar toN₂ of sputtering gas used in sputtering, the gas pressure, etc. However,since AlN has relatively large refractive index of approximately 1.8 to2.1, it is suitable for use as a material for the transparent dielectriclayer 2.

Moreover, the transparent dielectric layer 2 has not only a function ofenhancing the Kerr effect, but also a function of protecting the readoutlayer 3 or 3a and the recording layer 4 which are magnetic layers madeof a rare-earth transition metal alloy against oxidization together withthe protective film 6.

The magnetic film of rare-earth transition metal is oxidized easily, andespecially rare-earth metal is very easily oxidized. Therefore, in orderto prevent the deterioration of the properties of the layers, enteringof oxygen and moisture from outside must be prevented.

Thus, in this embodiment, the readout layer 3 or 3a, the recording layer4 and the auxiliary recording layer 5 are sandwiched between AlN films.The AlN films are nitrogen films which do not contain oxygen, and havehigh moisture resistance.

Furthermore, AlN has a relatively large refractive index of around 2, istransparent, and contains no oxygen. It is thus possible to provide amagneto-optical disk promising reliable performance for a long time.Additionally, with the use of an Al target, it is possible to perform areactive DC (direct current) sputtering by introducing N₂ gas or mixedgas of Ar and N₂. With this sputtering method, a faster film formingspeed is achieved compared with the RF (high frequency) sputteringmethod.

As for the materials for the transparent dielectric layer 2 other thanAlN, the following materials which have relatively large refractiveindexes are suitable: SiN, AlSiN, AlTaN, SiAlON, TiN, TiON, BN, ZnS,TiO₂, BaTiO₃ and SrTiO₃. In particular, since SiN, AlSiN, AlTiN, TiN, BNand ZnS do not contain oxygen, it is possible to provide amagneto-optical disk having an excellent moisture resistance.

SiN, AlSiN, AlTaN, SiAlON, TiN, TiON, BN, ZnS, TiO₂, BaTiO₃, SrTiO₃ areformed by sputtering. AlSiN, AlTaN, TiN and TiO₂ permit the reactive DCsputtering which is superior to the RF sputtering in terms of the filmforming speed. The refractive index of SiN, AlSiN, AlTaN, BN and ofSiAlON are in the range of 1.8 to 2.1. The refractive index of TiN is inthe range of 2 to 2.4. The refractive index of ZnS and of TiON are inthe range of 2 to 2.5. The refractive index of TiO₂, BaTiO₃ and ofSrTiO₃ are in the range of 2.2 to 2.8. These refractive indexes changedepending on the sputtering conditions.

Since the thermal conductivity of SiN and AlSiN is relatively small,they are suitable for a magneto-optical disk having high recordingsensitivity. Since AlTaN and TiN respectively include Ta and Ti, withthe use of these materials, a magneto-optical disk having an excellentcorrosion resistance is achieved. Since BN is extremely hard and has anexcellent abrasion resistance, the magneto-optical disk is preventedfrom having scratches, thereby ensuring a reliable performance for along time. The targets for ZnS, SiAlON and TiON are inexpensive. SinceTiO₂, BaTiO₃ and SrTiO₃ have extremely large refractive indexes, amagneto-optical disk ensuring a high quality reproduced signal isachieved.

In this embodiment, AlN used as the protective film 6 has a thickness of20 nm. However, the film thickness of the protective film 6 is notlimited to this, and it is preferably set in the range of 1 to 200 nm.

In this embodiment, the total film thickness of the readout layer 3 or3a, the recording layer 4 and the auxiliary recording layer 5 is set at150 nm. With this thickness, the laser light 8 hardly passes throughthese magnetic layers. Therefore, there is no limit for the filmthickness of the protective film 6 as long as the protective film 6 hasa film thickness which prevents oxidization for a long time. When amaterial which has low oxidization resistance is used, the filmthickness should be increased. On the other hand, when a material whichhas high oxidization resistance is used, the film thickness should bedecreased.

The thermal conductivity of the protective film 6 as well as thetransparent dielectric film 2 affects the recording sensitivity of themagneto-optical disk. More specifically, the recording sensitivityrepresents the laser power required for recording or erasing. Mostportions of the light incident on the magneto-optical disk aretransmitted through the transparent dielectric film 2, absorbed by thereadout layer 3 or 3a, the recording layer 4 and the auxiliary recordinglayer 5 which are absorbing films, and changed into heat. Here, heatgenerated from the magnetic layers is transferred to the transparentdielectric film 2 and the protective film 6 due to the conduction ofheat. Consequently, the respective thermal conductivities and thethermal capacities (specific heat) of the transparent dielectric film 2and the protective film 6 affect the recording sensitivity.

This means that the recording sensitivity of the magneto-optical diskcan be controlled to some extent by the film thickness of the protectivefilm 6. For example, by making the film thickness of the protective film6 thinner, the recording sensitivity is increased (a recording orerasing operation are carried out with low laser power). Normally, inorder to extend the life of the laser, it is preferable to haverelatively high recording sensitivity and the thinner protective film 6.

In this sense, AlN is a suitable material. Because of its excellentmoisture resistance, by using it as the protective film 6, it ispossible to reduce the film thickness and to provide a magneto-opticaldisk ensuring a high recording sensitivity.

In this embodiment, AlN is used for both the protective film 6 and, thetransparent dielectric film 2. Therefore, the magneto-optical disk ofthis embodiment has an excellent moisture resistance. Moreover, sincethe same material is used for the transparent dielectric film 2 and theprotective film 6, the productivity of the magneto-optical disk isimproved. As described above, since AlN has an excellent moistureresistance, it is possible to form the AlN film with a relatively thinfilm thickness of 20 nm. The thinner film is also preferable in terms ofproductivity.

Considering the above objectives and effects, other than AlN, thematerials: SiN, AlSiN, AlTaN, SiAlON, TiN, TiON, BN, ZnS, TiO₂, BaTiO₃and SrTiO₃ which can also be used as materials for the transparentdielectric film 2 are suitable for the protective film 6.

Additionally, by forming the protective film 6 and the transparentdielectric film 2 from the same material, the productivity is improved.

In particular, since SiN, AlSiN, AlTaN, TiN, BN and ZnS does not containoxygen, a magneto-optical disk having an excellent moisture resistanceis achieved.

Not only glass, but also chemically tempered glass is a suitablematerial for the substrate 1. Alternatively, a so-called 2P-layeredglass substrate which is formed by forming an ultraviolet rays-hardeningresin film on the glass or chemically tempered glass substrate,polycarbonate (PC), polymethyl methacrylate (PMMA), amorphous polyolefin(APO), polystyrene (PS), polybiphenyl chloride (PVC), epoxy, etc., maybe used for the substrate 1.

When chemically tempered glass is used as a material for the substrate1, the following advantages are obtained: excellent mechanicalproperties (in the case of a magneto-optical disk, vibration,eccentricity, warp, tilt, etc. ) are achieved; the hardness of thesubstrate 1 becomes large; sand or dust is not likely to adhere to thesubstrate because it is harder to be charged compared with the plasticsubstrate; it is not likely to be dissolved into various kinds ofsolvent as it is chemically stable; the moisture resistance, oxidizationresistance and thermal resistance are improved as it is chemicallytempered, and a reliable performance of the magneto-optical recordingmedium is ensured for a long time; and a high quality signal is obtaineddue to its excellent optical property.

Additionally, when the glass or chemically tempered glass is used as amaterial for the substrate 1, the reactive dry etching is carried out onthe surface of the glass substrate in order to form a guide track forguiding a light beam and produce a signal called a preformed pit on thesubstrate for recording an address signal, etc. The guide track or thepreformed pit may also be formed on the resin layer by applying aso-called 2P-layered ultraviolet rays-hardening resin, closely attachinga stamper on which tracks and pre-formed pits are formed, projecting alight beam thereto, and by removing the stamper.

When PC is used as a material for the substrate 1, an injection moldingis feasible. This allows the mass-production of the same substrate 1 anda reduction in the manufacturing cost. Since the substrate 1 made of PChas lower water absorption compared with other plastics, a reliableperformance of the magneto-optical disk is ensured for a longer time,and excellent heat resistance and impact resistance are achieved.Additionally, materials including PC which permit injection molding, aguide track, a preformed pit, etc., can be formed simultaneously on thesurface of the substrate 1 when molding if the stamper is installed on ametal molding mold in injection molding.

When PMMA is used as a material for the substrate 1, since the injectionmolding is feasible, a muss-production of the substrate 1 becomesavailable and the manufacturing cost is reduced. Such a substrate has asmaller double refraction compared with other plastics and an excellentoptical property. Thus, a high quality signal is ensured. In addition,the substrate 1 thus formed is durable.

Using APO as a material for the substrate 1 produces the followingadvantages. Since the injection molding is feasible, a muss-productionof the substrate 1 becomes available and the manufacturing cost isreduced. Since the substrate thus formed has a lower water absorptioncompared with other plastics, a reliable performance of themagneto-optical disk is ensured for a long time. Moreover, since thesubstrate 1 has a smaller double refraction compared with otherplastics, it has an excellent optical property, and a high qualitysignal is ensured. Furthermore, the substrate 1 has high heat resistanceand impact resistance.

Using PS as a material for the substrate 1 gives the followingadvantages. Since the injection molding is feasible, a muss-productionof the substrate 1 becomes available and the manufacturing cost isreduced. Since the substrate thus formed has a lower absorbance comparedwith other plastics, a reliable performance of the magneto-optical diskis ensured for a long time.

Using PVC as a material for the substrate 1 produces the followingadvantages. Since the injection molding is feasible, a muss-productionof the substrate 1 becomes available and the manufacturing cost isreduced. Since the substrate thus formed has a lower absorbance comparedwith other plastics, a reliable performance of the magneto-optical diskis ensured for a long time. Moreover, the substrate 1 is fire retardant.

Using epoxy as a material for the substrate 1 produces the followingadvantages. Since the injection molding is feasible, a muss-productionof the substrate 1 becomes available and the manufacturing cost isreduced. Since the substrate thus formed has a lower absorbance comparedwith other plastics, a reliable performance of the magneto-optical diskis ensured for a long time. Moreover, the substrate 1 is formed by athermosetting resin, it has an excellent heat resistance.

As described, various materials may be used for the substrate 1.However, when using the above materials for the substrate 1 of themagneto-optical disk, it is desired that a selected material has thefollowing optical and mechanical properties:

refractive index: 1.44-1.62

double refraction: not more than 100 nm (double refraction measured by aparallel beam)

transmittance: not less than 90%

variation in thickness: ±0.1 mm

tilt: not more than 10 mrad

vibration acceleration: not more than 10 m/s²

radial direction acceleration: not more than 3 m/s².

The optical pickup for conversing a laser beam onto the recording layer4 is designed by taking account of the refractive index of thesubstrate 1. Therefore, if the refractive index of the substrate 1 ischanged to a large degree, the laser light 8 cannot be convergedsufficiently. Furthermore, if the laser beam is not converged in auniform manner, the temperature distribution of the recording medium(readout layer 3 or 3a and the recording layer 4) is subjected tochange, affecting the recording and reproducing operations. In thepresent invention, the temperature distribution of the recording mediumduring reproduction is especially important. It is therefore desirableto set the refractive index of the substrate 1 within a range of 1.44 to1.62.

Since the laser light 8 is incident on the recording medium through thesubstrate 1, if double refraction occurs in the substrate 1, thepolarization state changes when the laser light 8 passes through thesubstrate 1. With the structure of the present invention, a change inthe magnetic state of the readout layer 3 or 3a is recognized as achange in the polarization state by utilizing the Kerr effect duringreproduction. Therefore, if the polarization state changes when thelaser light 8 is transmitted through the substrate 1, a reproducingoperation cannot be carried out. For this reason, double refraction ofthe substrate 1 is desired to be below 100 nm when measured by parallellight.

Also, if the transmittance of the substrate 1 becomes lower, forexample, a reduced amount of a light beam is transmitted from theoptical pickup through the substrate 1 during recording. Therefore, inorder to retain a sufficient light amount for recording, a laser sourcewhich generates a higher output is required. Especially, with thestructure of the present invention, since the recording medium has adouble-layer structure composed of the recording layer 4 and the readoutlayer 3 or 3a, a greater amount of light is required for raising thetemperature of the recording medium compared with the conventionalrecording medium of a single-layer structure (having no readout layers 3and 3a). For this reason, the transmittance of the substrate 1 ispreferably set to or above 90%.

The optical pickup for converging the laser light 8 on the recordingmedium is designed by taking account of the thickness of thesubstrate 1. Therefore, if the thickness of the substrate 1 varies to agreat degree, the laser light 8 cannot be converged sufficiently.Furthermore, if the laser light 8 is not converged under the stablecondition, the temperature distribution of the recording medium ischanged, thereby adversely affecting the recording and reproducingoperations. With the present invention, the temperature distribution ofthe recording medium during reproduction is especially important. It istherefore desirable to restrain the variation in the thickness of thesubstrate 1 within a range of ±0.1 mm.

If the substrate 1 is tilted, the laser light 8 from the optical pickupis converged on the tilted recording medium surface. Namely, theconverged state changes depending on the degree of tilt. Thus, thevariation in the thickness of the substrate 1 adversely affectsrecording and reproducing operations. In the present invention, the tiltof the substrate 1 is set below 10 mrad, more preferably below 5 mrad.

When the substrate 1 is moved up and down with respect to the opticalpickup, the optical pickup is activated so as to compensate for themovement and to converge the laser light on the surface of the recordingmedium. However, if the substrate 1 is largely moved up and down, itbecomes impossible to activate the optical pickup so as to completelycompensate for the movement. Therefore, the laser light 8 cannot beconverged on the recording medium sufficiently. This changes thetemperature distribution of the recording medium, thereby adverselyaffecting recording and reproducing operations. In the presentinvention, since the temperature distribution of the recording mediumduring reproducing is especially important, the vibration accelerationin the up and down movement of the rotating substrate 1 is preferablyset to or below 10 m/s².

On the substrate 1, the guide track for guiding a light beam is formedbeforehand at 1.0 to 1.6 μm pitch. However, if the guide track iseccentric, the guide track moves in a radial direction with respect tothe optical pickup when the disk is rotated. In this case, the opticalpickup is activated to compensate for the movement in a radial directionand to converge the laser light 8 so as to maintain a predeterminedrelationship with the guide track. However, if the movement of the guidetrack in a radial direction becomes excessively large, it becomesimpossible to activate the optical pickup so as to sufficientlycompensate for the movement. Thus, the laser light 8 cannot be convergedwhile keeping a predetermined relationship with the guide track. Asdescribed above, in the present invention, the temperature distributionof the recording medium during reproduction is especially important. Asfor the movement of the guide track in a radial direction when thesubstrate i is rotated, it is therefore desirable to set theacceleration in a radial direction to or below 3 m/s².

There are two methods for converging the laser light 8 onto apredetermined position on the magneto-optical disk: successive servosystem utilizing a spiral or concentric guide track; and a sample servosystem utilizing a spiral or concentric pit string.

As shown in FIG. 23, with the successive servo system, grooves areformed to have a width of 0.2 to 0.6 μm, a depth of substantially λ/(8n)and at a pitch of 1.2 to 1.6 μm. Generally, recording and reproducing ofinformation are carried out on and from lands of a so-called land-usemagneto-optical disk. Here, λ indicates a wavelength of a laser beam,and n indicates the refractive index of the substrate 1 to be used.

It is possible to adapt the present invention to such a generally usedmethod. With the present invention, crosstalk from recording bits onadjacent tracks is reduced to a great degree. Therefore, for example,with the land-use magneto-optical disk, even when grooves are formedwith a width of 0.1 to 0.4 μm and at a pitch of 0.5 to 1.2 μm, recordingand reproducing operations can be carried out without having an adverseeffect of the crosstalk from the adjoining recording bits, resulting ina significant increase in the recording density.

As shown in FIG. 24, when recording and reproducing operations arecarried out on and from lands and grooves which are formed to have thesame width and at a pitch of 0.8 to 1.6 μm, recording and reproducingoperations can be carried out without having an adverse effect of thecrosstalk from the adjoining recording bits. This structure results inan significant improvement of the recording density.

When the sample servo system is adapted, as shown in FIG. 25, a wobblypit is formed beforehand with a depth of substantially (λ/(4n)) and at apitch of 1.2 to 1.6 μm. In general, recording and reproducing ofinformation are carried out so as to scan the center of the wobbly pitwith the laser beam.

It is possible to adapt the present invention to such a generally usedmethod. With the present invention, crosstalk from recording bits on theadjacent tracks can be reduced to a great degree. Therefore, informationis recorded and reproduced on/from a magneto-optical disk having wobblypits formed at a pitch of 0.5 to 1.2 μm without having an adverse effectof the crosstalk from the adjoining recording bits. This structureenables a significant improvement of the recording density.

As shown in FIG. 26, wobbly pits are formed at a pitch of 0.8 to 1.6 μm,and recording and reproducing of information are carried out in an areahaving a wobbly pit of opposite polarity. With this structure, recordingand reproducing operations can be carried out without having an adverseeffect of the crosstalk from the adjoining recording bits, therebysignificantly improving the recording density.

As shown in FIG. 27, with the successive servo system, when informationindicative of position on the magneto-optical disk is obtained bywobbling the grooves, the crosstalk from the recording bits on theadjoining grooves becomes large in the area having a phase opposed tothe wobbling state. However, with the present invention, crosstalk fromthe recording bits on the adjoining grooves is prevented even in thearea having the opposed wobbling state, thereby achieving preferablerecording and reproducing operations.

Moreover, the magneto-optical disk of this embodiment is used with avariety of the following recording and reproducing optical pickups.

For example, when an optical pickup of a multiple beam system using aplurality of light beams is used, it is generally positioned such thatamong a plurality of light beams, the light beams on both ends scan theguide track, and recording and reproducing operations are carried outusing the light beams between them. However, with the use of themagneto-optical disk of the present invention, even when the width ofthe light beam is reduced, a reproducing operation can be carried outwithout having an adverse effect of the crosstalk from the adjoiningrecording bits, and thus the pitch of the guide track is shortened.Alternatively, a greater number of laser beams can be used between apair of guide tracks for recording and reproduction so as to achieve aneven higher density recording and reproduction.

In the above explanation, the guide track pitch, etc., has beendiscussed by assuming that the number of aperture (N.A.) of theobjective lens of the optical pickup is in a range of 0.4 to 0.6 whichis a generally used value, and the wavelength of the laser light is in arange of 670 to 840 nm. However, by increasing the N.A. to a range of0.6 to 0.95, a laser beam is converged into a smaller spot, and byadapting the magneto-optical disk of the present invention, the pitchand the width of the guide track is made still narrower, therebypermitting a still higher recording and reproducing density.

Additionally, using an argon laser beam with a wavelength of 480 nm or alaser beam with a wavelength of 335 to 600 nm utilizing a SHG elementenables the laser beam to be converged into a smaller spot. Further,using the present invention enables the pitch and the width of the guidetrack to be made still smaller. Consequently, still higher densityrecording and reproducing operations are achieved.

a/w in a range of 0.3 to 1.0 may be used. Here, a represents opticallyeffective diameter of the lens, and w represents a radius at which theintensity of the light beam is 1/e² of the central intensity of thelight beam when the intensity of the light beam shows Gaussiandistribution.

The following description discusses the disk format to be adapted in themagneto-optical disk of this embodiment.

In general, in order to maintain the compatibility betweenmagneto-optical disks of different brands and of different types, avalue and a duty of the power required in recording and erasing at eachradial position are recorded beforehand in the form of a pre-formed pitstring with a depth of substantially (λ/(4n)) in a part of inner orouter circumference. Moreover, based on the read values, a test area isprovided in inner or outer circumference to allow recording andreproducing tests (for example, see IS10089 standard).

As for the reproducing power, information which indicates a reproducingpower is recorded beforehand in a portion of an inner or outercircumference in a form of a preformed pit string.

With the present invention, the temperature distribution of therecording medium during reproduction largely affects the reproducingperformance. It is therefore extremely important to determine thereproducing power.

As a method for setting a reproducing power, for example, the followingmethod is preferable. Like the recording power, a test area for settinga reproducing power is provided on an inner or outer circumference, andinformation for optimizing the reproducing power which is obtained fromthe test area for each radial position is preferably recorded in advanceon a part of an inner or outer circumference in a form of a pit string.

Especially, when a magneto-optical disk player which adapts a CAV systemfor producing a constant rotating speed, since the linear velocity ofthe magneto-optical disk changes depending on the radial position, thereproducing laser power is preferably adjusted for each radial position.Therefore, information segmented into as many areas as possible in aradial direction is preferably recorded in a form of a preformed pitstring.

As a method for determining an optimum reproducing laser power at eachradial position, the following method is also available. A recordingarea is divided into a plurality of zones according to a radialposition, and the optimum recording power and the reproducing power aredetermined using the test areas provided in the respective boundaries ofthe zones, thereby permitting accurate control of the temperaturedistribution of the recording medium during reproduction. This methodallows preferable recording and reproducing operations.

The magneto-optical disk of this embodiment is applicable to a variousrecording system as explained below.

A method for recording information on the first generation ofmagneto-optical disks incapable of overwriting is described first.

A first-generation magneto-optical disk under IS10089 standard (ISOstandard set for 5.25" rewritable optical disk) has been sold a lot.Since overwriting is unavailable with this type of magneto-optical disk,in order to write new information on a portion which has alreadycontained information, the previously recorded information must beerased from the portion before recording the new information. Namely, atleast two rotations of the magneto-optical disk are required to writethe new information. Thus, the first generation of magneto-optical diskssuffer from low data transfer speeds.

However, the first generation of magneto-optical disks have such anadvantage that a requirement for the magnetic films is not as high asfor magneto-optical disks capable of overwriting (to be describedlater).

In order to permit overwriting, for example, the following method hasbeen used by some devices. With this method, a plurality of opticalheads are provided to eliminate the time loss caused by waiting and toimprove a data transfer speed.

More specifically, when two optical heads are used, a first optical headis used for erasing recorded information; and a second optical headwhich follows the first optical head is used for recording newinformation. For reproduction, either the first or second optical headis used.

In the case where three optical heads are used, the first optical headis used for erasing the recorded information, the second optical head isused for recording new information, and a third optical head is used forverifying if new information is accurately recorded.

It is also possible to perform overwriting using a single optical headinstead of a plurality of optical heads by producing a plurality oflight beams with a beam splitter.

These structures allow recording of new information without erasing thepreviously recorded information. Thus, virtual overwriting is availablewith a first-generation magneto-optical disk.

Since the magneto-optical disk of this embodiment permits recordinginformation on the recording layer 4 by controlling the magnetizationdirection of the readout layer 3 or 3a and of the auxiliary recordinglayer 5 with a recording magnetic field. It is thus possible to use therecording method with the magneto-optical disk of this embodiment.

Next, the magnetic-field modulation overwriting system is explained.

By the magnetic-field modulation overwriting system, information isrecorded on the recording layer 4 by controlling the magnetizationdirection of the readout layer 3 or 3a and the auxiliary recording layer5 with a recording magnetic field. It is thus possible to adapt therecording method.

With the magnetic-field modulation overwriting system, recording isperformed by modulating the intensity of the magnetic filed inaccordance with the information while projecting a laser light of auniform power onto the magneto-optical recording medium. Themagnetic-field modulation overwriting system is explained below in moredetail with reference to FIG. 29.

FIG. 31 is a typical depiction which shows one example of themagneto-optical disk player which overwrites information on amagneto-optical disk 24 by the magnetic-field modulation. The device isprovided with a light source (not shown) for projecting the laser light8 for recording and reproduction, an optical head 21 including areceiving element (not shown) for receiving a reflected light from themagneto-optical disk 24 during recording and reproduction, and afloating-type magnetic head 22 which is electrically or mechanicallyconnected to the optical head 21.

The floating-type magnetic head 22 is composed of a floating slider 22aand a magnetic head 22b which includes a core made of MnZn ferrite,etc., having a coil wound around thereon. The floating-type magnetichead 22 is pressed down toward the magneto-optical disk 24 so as tomaintain a predetermined distance of approximately several μm to severaltens μm.

In this state, the floating-type magnetic head 22 and the optical head21 are moved to a desired radial position in the recording area of themagneto-optical disk 24, and the laser light 8 with a power of 2 to 10mW from the optical head 21 is converged thereon to raise thetemperature of the recording layer 4 to the vicinity of Curietemperature (or the temperature at which coercive force becomes nearlyzero). In this state, a magnetic field whose magnetization direction isreversed upward and downward in accordance with information to berecorded is applied from the magnetic head 22b. Thus, information isrecorded by the overwriting system without including an erasing processof previously recorded information.

In this embodiment, the laser power used in overwriting by themagnetic-field modulation is set uniform. However, when the polarity ofthe magnetic field changes, if the laser power is reduced to a power atwhich recording is infeasible, the shape of the recording bit isimproved, thereby resulting in a reproduced signal of improved quality.

The magneto-optical disk 24 is of a so-called single sided type. Thethin films of the magneto-optical disk 24, i.e., the transparentdielectric film 2, the readout layer 3 or 3a, the recording layer 4 andthe protective film 6 are referred to as a recording medium layer.Namely, the magneto optical disk 24 is composed of the substrate 1, arecording medium layer 29 and the overcoat film 7 as shown in FIG. 30.

A so-called both sided magneto-optical disk is shown in FIG. 29. In themagneto-optical disk of this type, a pair of the substrates 1 whereonthe recording medium layers 29 are respectively laminated by an adhesivelayer 30 so that respective recording magnetic layers 29 face eachother.

As for the material for the adhesive layer 30, a polyurethane acrylateseries adhesive agent is particularly preferable. The above adhesiveagent has a combination of the hardening properties under an applicationof ultraviolet rays, heat and anaerobic. Thus, a shadow portion of therecording medium layer 29 which does not allow the ultraviolet rays topass through is hardened by heat and anaerobic. It is therefore possibleto provide a double-sided magneto-optical disk which has extremely highmoisture resistance, ensuring a reliable performance for a long time.

On the other hand, since the single-sided magneto-optical disk has athickness which is a half of the thickness of the double-sidedmagneto-optical disk, it is suitable for use in a compactmagneto-optical recording and reproducing device, for example.

The double-sided magneto-optical disk is suitable for use in a largecapacity recording and reproducing device because information isreproducible from both sides thereof.

When determining which type of the magneto-optical disk is suitable, thethickness and the capacity of the magneto-optical disk should beconsidered as explained above. In addition, as explained below, arecording method is needed to be carefully selected when determining atype of the magneto-optical disk to be used.

As well known, information is recorded on the magneto-optical disk usinga light beam and a magnetic field. As shown in FIG. 29, in themagneto-optical disk player, a light beam emitted from a light sourcesuch as a semiconductor laser is converged on the recording medium layer29 through the substrate 1 by the converging lens. Additionally, amagnetic field is applied to the recording medium layer 29 by a magneticfield generation device such as a magnet and an electro-magnet (forexample, floating-type magnetic head 22), disposed to face the lightsource. When recording, by setting the light beam intensity higher thanthe light beam used for reproducing, the temperature of the portion ofthe recording medium layer 29 exposed to the converged light beam israised. As a result, a coercive force of the magnetic film at theportion becomes smaller. In this state, by externally applying amagnetic field larger than the coercive force, the magnetizationdirection of the magnetic film is aligned with the magnetizationdirection of the applied magnetic field, thereby completing therecording process.

For example, by the magnetic-field modulation overwriting method whereinthe recording-use magnetic field is modulated according to theinformation to be recorded, the magnetic field generating device (mostlyan electro-magnet) is needed to be disposed closer to the recordingmedium layer 29. The reason for this is that, due to the limitations ofheat generation by the coil of the electro-magnet, electric powerconsumption of the device and the size of magnetic field generatingdevice, etc., when generating a magnetic field required for recording(generally 50 Oe to several hundreds Oe) by modulating at a frequencyrequired for recording (usually, several hundreds kHz to several tensMHz), the magnetic field generating device is needed to be disposed sothat the distance between the magnetic filed generating device and themagneto-optical disk is about 0.2 mm or less, more preferably about 50μm. In the case of the both-sided magneto-optical disk, the thickness ofthe substrate 1 is at least 0.5 mm and normally 1.2 mm. Thus, when theelectro-magnet is placed to face the light beam, the magnetic fieldsufficient for recording cannot be ensured. For this reason, when therecording medium layer 29 suitable for overwriting by the magnetic-fieldmodulation is adapted, a single-sided magneto-optical disk is oftenused.

Meanwhile, in the case of the overwriting method by the light-intensitymodulation wherein a light beam is modulated according to information tobe recorded, recording can be carried out with a uniform magnetic fieldH_(B) whose magnetization is fixed in one direction. Therefore, forexample, a permanent magnet which has a magnetic filed of high intensityis used. Thus, unlike the magnetic-field modulation, there is no need todispose the magnetic field generating device in a position closest tothe recording medium layer 29. It is therefore possible to dispose themagnetic filed generating device in a position several mm away from therecording medium layer 29. Consequently, not only the single-sided typebut also doubly-sided type magneto-optical disk can be used.

If the magneto-optical disk of this embodiment is of a single-sidedtype, it may have various structures as follows.

A first example of a magneto-optical disk has a hard coat layer, notshown, on the overcoat film 7. More specifically, the magneto-opticaldisk is composed of the substrate 1, the recording medium layer 29, theovercoat film 7 and a hard coat layer. As for the hard coat layer, forexample, a film of an acrylate series ultraviolet rays-hardening typehard coat resin film (hard coat layer) is formed on the overcoat film 7which, for example, is made of a polyurethane acrylate seriesultraviolet rays-hardening resin with a thickness of substantially 6 μm.The hard coat layer may be formed with a film thickness of 3 μm.

With this structure, since the overcoat film 7 is formed, thedeterioration of the property of the recording medium layer 29 due tothe oxidization is prevented, thereby ensuring reliable recording andreproducing operations for a long time. Additionally, since the hardcoat layer which is made of a hard material and has large wearresistance is provided, even if the magnet for use in recording comesinto contact with the disk, the disk hardly has scratches, or even if ithas scratches, the scratches would not reach the recording medium layer29.

Needless to say, it is possible to omit the hard coat layer if theovercoat film 7 is designed to have the function of the hard coat layer.

A second example of the single-sided magneto-optical disk of thisembodiment has a hard-coat layer formed on the overcoat film 7, and ahard-coat layer, not shown, formed on a side of the substrate 1 wherethe recording medium layer 29 is not formed. Namely, the magneto-opticaldisk is composed of a hard coat layer, the substrate 1, the recordingmedium layer 29, the overcoat film 7, and another hard coat layer.

As for the material for the substrate 1 of the magneto-optical disk, aplastic such as PC is generally used. However, since the plastic is verysoft compared with a glass material, it easily has scratches even byrubbing with a nail. If the disk has deep scratches, a servo jump mayoccur. This may cause the recording and reproducing operations to beinfeasible.

When reproducing information from the magneto-optical disk of thisembodiment, only the center portion of the light beam is used. Thus, incomparison with a conventional magneto-optical disk, the defectivenessof the surface of the substrate 1 such as scratches more adverselyaffects reproduction. In order to overcome such a problem, the hard coatlayer is provided on the side of the substrate 1 where the recordingmedium layer 29 is not formed. This structure is very effective forpreventing scratches on the disk.

The same effect can be produced by the double-sided magneto-optical diskby providing a hard coat layer on both the surfaces of the substrate 1.

A third example of the magneto-optical disk has a charge preventing coatlayer (not shown) formed on the overcoat film 7 or the hard coat layerof the first or the second example. The magneto-optical disk may includea layer having a charge preventing function instead of the chargepreventing coat layer.

Like the problem caused by scratches, if the dust adheres to the surfaceof the substrate 1, recording and reproduction of information may becomeinfeasible. When the overwriting method by the magnetic-field modulationis adopted and when a magnet as the floating-type magnetic head 22 (FIG.29) is placed several μm above the overcoat film 7, if dust adheres ontothe overcoat film 7, the floating-type magnetic head 22 and therecording medium layer 29 get damaged due to the dust.

However, with the structure of this embodiment, since a layer having acharge preventing function is formed on a surface of the magnet-opticaldisk on the substrate 1 side or the recording medium layer 29 side, itis possible to prevent dust from adhering to the substrate 1 and theovercoat film 7.

When reproducing information from the magneto-optical disk of thisembodiment, only a center portion of the light beam is used. Therefore,the defectiveness of the surface of the substrate 1 such as dust morebadly affects the reproduction compared with the conventional case.Thus, the above-mentioned structure for preventing dust adhering to thesurface of the substrate 1 is very effective.

As for the charge preventing layer, for example acrylic series hard coatresin into which an electrically conductive filler is mixed is used. Thecharge preventing layer is preferably formed to have a thickness ofabout 2 to 3 μm.

The charge preventing film is provided to decrease the surfaceresistance and to prevent dust from adhering to the surface of thesubstrate 1 irrespectively of the material of the substrate 1, i.e.,plastic or glass.

Needless to say, it is also possible to produce the overcoat film 7 orthe hard coat layer having a charge preventing effect.

This structure is also applicable to both the surfaces of the substrate1 of a double-sided magneto-optical disk.

A fourth example of the magneto-optical disk has a lubricant film (notshown) formed on the overcoat film 7. Namely, the magneto-optical diskis composed of the substrate 1, the recording medium layer 29, theovercoat film 7 and the lubricant film. A fluorocarbon series resin is amaterial suitable for the lubricant film. The preferable film thicknessof the lubricant film is substantially 2 μm.

When performing the magnetic-field modulation overwriting using thefloating-type magnetic head 22, since the lubricant film is provided,the lubrication between the floating-type magnetic head 22 and themagneto-optical disk is improved.

The floating-type magnetic head 22 is positioned several μm to severaltens μm above the recording medium layer 29. Namely, the space betweenthe floating-type magnetic head 22 and the recording medium layer 29 ismaintained by balancing the pressing force produced by a suspension 23and the floating force generated by the air flow due to the rotation ofthe disk. The pressing force presses the floating magnetic head 22toward the recording medium layer 29, while the floating force causesthe floating magnetic head 22 to apart from the recording medium layer29. The floating force is generated by a flow of air which is causedwhen the magneto-optical disk is rotated at high speeds.

If the floating-type magnetic head 22 is used together with the CSS(contact-Start-Stop) method in which the floating-type magnetic head 22and the magneto optical disk are in contact with one another from thestart of rotating the disk until the magneto-optical disk is rotated ata predetermined speed, and until the disk is completely stopped afterthe switch is turned off, a problem may arise. Namely, if thefloating-type magnetic head 22 adheres to the magneto-optical disk, thefloating-type magnetic head 22 may get damaged when the magneto-opticaldisk is started rotating. However, with the structure of themagneto-optical disk of this embodiment, since a lubricant film isformed on the overcoat film 7, the lubrication between the floating-typemagnetic head 22 and the magneto-optical disk is improved, and therebypreventing the floating-type magnetic head 22 from getting damaged.

Needless to say, if a moisture resistant protective material whichprevents the deterioration of the recording medium layer 29 is used, itis not necessary to provide the overcoat film 7 and the lubricant filmseparately.

A fifth example of the magneto-optical disk of this embodiment has amoisture-proof layer (not shown) and a second overcoat film (not shown)formed on a side of the substrate 1 where the recording medium layer 29is not formed. Namely, the magneto-optical disk is composed of thesecond overcoat film, the moisture-proof layer, the substrate 1, therecording medium layer 29 and the overcoat film 7.

As for the material for the moisture-proof layer, a transparentdielectric material such as AlN, AlSiN, SiN, AlTaN, SiO, ZnS, TiO₂, maybe used, and the suitable thickness for the moisture-proof layer isapproximately 5 nm. The second overcoat film is effective especiallywhen a high moisture permeability plastic material such as PC is usedfor the substrate 1.

The moisture-proof layer is effective to minimize the warping of themagneto-optical disk due to a change in environmental moisture. Thefollowing description discusses the effect in detail.

If the moisture-proof layer is not provided, for example, when theenvironmental moisture changes largely, moisture is absorbed or releasedin or from only the side of the substrate 1 where the recording mediumlayer 29 is not provided, i.e., the light incident side of the plasticsubstrate 1. The moisture absorption and release causes a partial changein the volume of the plastic substrate 1, resulting in the warpedplastic substrate 1.

When the substrate 1 warps, it tilts with respect to the axis of thelight beam used in reproducing or recording information. As a result, aservo does not operate properly, and the signal quality is lowered. Inthe worst case, a servo may skips.

Additionally, if the substrate 1 tilts, the laser light 8 from theoptical head 21 (see FIG. 29) is converged on the surface of the tiltedrecording medium layer 29. The converged state thus changes depending onthe degree of tilt. This adversely affects the recording and reproducingoperations.

Furthermore, when the substrate 1 is moved up and down with respect tothe optical head 21, the optical head 21 is activated to compensate forthe movement of the substrate 1 and to converge the laser light 8 on thesurface of the recording medium layer 29. However, when the upward anddownward movement of the substrate 1 is excessively large, the opticalhead 21 cannot fully compensate for the movement. As a result, the laserlight 8 cannot be converged on the recording medium layer 29 properly.This causes a change in the temperature distribution of the recordingmedium layer 29, affecting the recording and reproducing operations.With the structure of this embodiment, since the temperaturedistribution of the recording medium layer 29 during reproduction isparticularly important, it is necessary to minimize the warp of thesubstrate 1 and the change in the warping degree caused by environmentalchanges.

With this structure of the magneto-optical disk, since themoisture-proof layer prevents the front surface of the substrate 1 fromabsorbing and releasing moisture, the warp of the substrate 1 issignificantly minimized. This structure is therefore particularlysuitable for the present invention.

The second overcoat film on the moisture-proof layer prevents themoisture-proof layer from having scratches and protects the surface ofthe substrate 1. The second overcoat film may be formed by the samematerial used for the overcoat film 7 on the recording medium layer 29.

The hard coat layer or the charge preventing layer may be providedinstead of the second overcoat film or on the second overcoat film.

The following description discusses a fifth embodiment of the presentinvention with reference to FIG. 32. The members having the samefunction as in the above-mentioned embodiments will be designated by thesame code and their description will be omitted.

As illustrated in FIG. 32, a magneto-optical recording disk of thisembodiment is composed of the substrate 1 having thereon the transparentdielectric film 2, the readout layer 3a, the recording layer 4, theauxiliary recording layer 5, a radiating layer 12 and the overcoat film7 formed in this order.

As for the material for the radiating layer 12, Al may be used, and thefilm thickness is preferably set in the vicinity of 100 nm. As for thematerials for the substrate 1, the transparent dielectric film 2, thereadout layer 3a, the recording layer 4, the auxiliary recording layer 5and the overcoat film 7, the materials used in the previous embodimentsmay be used.

The magneto-optical disk of this embodiment is constructed by formingthe radiating layer 12 on the auxiliary recording layer 5 of themagneto-optical disk of the second embodiment. This magneto-optical diskthus has the following function and effect in addition to the functionand effect of the disk of the second embodiment.

In this embodiment, since the radiating layer 12 is formed on theauxiliary recording layer 5, the shape of the recording bit issharpened. The reasons for this are as follows.

Most of the light beam applied to the magneto-optical disk from thelight incident side is absorbed by the readout layer 3a, the recordinglayer 4 and the auxiliary recording layer 5, and converted into heat. Atthis time, the heat is conducted in a vertical direction of the readoutlayer 3a, the recording layer 4 and the auxiliary recording layer 5, andis also conducted in a horizontal direction of the layers. When a largeamount of heat is conducted in the horizontal direction at a low speed,if high density recording is to be performed at higher speeds, therecording bit to be recorded next is thermally affected adversely. Ifthis occurs, the length of the recording bit becomes longer than apredetermined length or the size of the recording bit is expanded in adirection orthogonal to the track direction. If the recording bit isexpanded in the direction orthogonal to the track direction, the amountof crosstalk may increase, thereby preventing proper recording andreproducing operations.

In this embodiment, the radiating layer 12 made of Al having the highthermal conductivity is formed on the auxiliary recording layer 5. Theheat conducted is released toward the radiating layer 12, i.e., in avertical direction, thereby reducing the spread of heat in the directionperpendicular to the track direction. Consequently, recording is carriedout without having a thermal interference under the high density andhigh speed recording conditions.

Inclusion of the radiating layer 12 provides the following advantages inoverwriting by light-intensity modulation.

Since the radiating layer 12 is provided, in the process of recording,when the area whose temperature has been raised by the projection of thelight beam is cooled down, the differences in the change of thetemperatures among the readout layer 3a, the recording layer 4 and theauxiliary recording layer 5 are made more significant. Hence, theoverwriting by the light-intensity modulation is more easily performed.

Al used for the radiating layer 12 has a higher thermal conductivitycompared with the film of the rare-earth transition metal alloy used forthe readout layer 3a, the recording layer 4 and the auxiliary recordinglayer 5. Thus, Al is a suitable material for the radiating layer 12.Additionally, since AlN is formed by reactively sputtering an Al targetby Ar and N₂ gas, the radiating layer 12 can be easily formed bysputtering the same Al target by Ar gas. Al is a considerablyinexpensive material.

A sample (#5-1) of a magneto-optical disk as the magneto-opticalrecording medium of this embodiment is explained below.

The substrate 1 is made of a disk-shaped glass with a diameter of 86 mm,an inner diameter of 15 mm and a thickness of 1.2 mm. Although it is notshown, lands and grooves are formed on a surface of the substrate 1 toproduce a guide track for guiding a light beam. The track is formed at apitch of 1.6 μm, with a groove width of 0.8 μm and a land width of 0.8μm.

AlN with a thickness of 80 nm is formed as the transparent dielectriclayer 2 on the surface of the substrate 1 whereon the guide track isformed.

The readout layer 3a, the recording layer 4 and the auxiliary layer 5are formed on the transparent dielectric layer 2.

For the readout layer 3a, a thin film of rare-earth transition metalalloy made of GdFeCo with a thickness of 50 nm is formed on thetransparent dielectric layer 2. The composition of GdFeCo is Gd₀.29(Fe₀.82 Co₀.18)₀.71, and the Curie temperature thereof is around 280° C.

For the recording layer 4, a thin film of rare-earth transition metalalloy made of DyFeCo with a thickness of 50 nm is formed on the readoutlayer 3a. The composition of DyFeCo is Dy₀.23 (Fe₀.78 Co₀.22)₀.77, andthe Curie temperature thereof is around 200° C.

The combination of the readout layer 3a and the recording layer 4 causesthe readout layer 3a to have substantially in-plane magnetization atroom temperature and to have perpendicular magnetization within thetemperature range between 100° and 125° C.

For the auxiliary recording layer 5, a thin film of rare-earthtransition metal alloy made of GdFeCo with a thickness of 50 nm isformed on the recording layer 4. The composition of GdFeCo is Gd₀.17(Fe₀.82 Co₀.18)₀.83, and the Curie temperature thereof is around 320° C.

AlN with a thickness of 100 nm is placed as the radiating layer 12 onthe auxiliary recording layer 5.

A polyurethane acrylate series ultraviolet rays-hardening resin with athickness of 5 μm is placed as the overcoat film 7 on the radiatinglayer 12.

The suitable material for the radiating layer 12 is not limited to Al.Other material may be used as long as it has a larger thermalconductivity than the readout layer 3a, the recording layer 4 and theauxiliary recording layer 5. For example, Au, Ag, Cu, SUS, Ta or Cr areused.

When using Au, Ag or Cu for the radiating layer 12, a reliableperformance of the film is ensured for a long time because they havehigh resistance against oxidization, humidity and corrosion.

When using SUS, Ta or Cr for the radiating layer 12, a reliableperformance of the film is ensured for a long time because they haveextremely high resistance against oxidization, humidity and corrosion.

In this embodiment, the thickness of the radiating layer 12 is set at100 nm. The thicker the radiating layer 12, the larger the radiatingeffect. Consequently, long-time reliability is improved by increasingthe film thickness. However, in considering the recording sensitivity ofthe magneto-optical disk as described earlier, it is necessary todetermine the film thickness in accordance with the thermal conductivityand the specific heat. Namely, the film thickness is preferably setwithin a range of 5 to 200 nm, and more preferably within a range of 10to 100 nm. By using the material having a relatively high heatconductivity and high resistance against corrosion, it is possible tomake the film thickness in a range of 10 to 100 nm, thereby reducing thetime required for forming the film.

It may possible to insert a dielectric layer, not shown, between theauxiliary recording layer 5 and the radiating layer 12. The preferablefilm thickness of the dielectric layer is between 10 and 100 nm. As forthe material, the same material used for the transparent dielectriclayer 2 may be used. For example, the materials used in theabove-mentioned embodiments, such as AlN, SiN, and AlSiN, etc. are used.In particular, by using a nitride film such as AlN, SiN, AlSiN, TiN,AlTaN, ZnS, and BN which do not contain oxygen, a magneto-optical diskensuring a reliable performance for a longer time is provided.

As described above, the magneto-optical recording medium of the presentinvention does not require an initializing magnetic field.

In the above-mentioned embodiments, the magneto-optical disk isdiscussed as the magneto-optical recording medium. However, the presentinvention is also applied to a magneto-optical card, magneto-opticaltape, etc. Additionally, in the case of the magneto-optical tape,instead of the rigid substrate 1, a flexible tape base, for example, abase made of polyethylene terephtalate may be used.

The invention being thus described, it will be obvious that the same maybe varied in many ways. Such variations are not to be regarded as adeparture from the spirit and scope of the invention, and all suchmodifications as would be obvious to one skilled in the art are intendedto be included within the scope of the following claims.

What is claimed is:
 1. A magneto-optical recording medium comprising:abase; a readout layer formed on said base; a recording layer formed onsaid readout layer; an auxiliary recording layer formed on saidrecording layer, each of said readout layer, recording layer andauxiliary recording layer comprising an alloy of rare-earth metalexhibiting ferrimagnetism and transition metal, said alloy compositionof each of said readout layer, said recording layer and said auxiliaryrecording layer being such that said recording layer has a Curietemperature lower than Curie temperatures of said readout layer and saidauxiliary recording layer, and said recording layer has a coercive forcehigher than coercive forces of said readout layer and said auxiliaryrecording layer at room temperature and that, when a temperature of saidrecording layer is raised to a temperature approximately equal to itsCurie temperature while perpendicularly applying a uniform recordingmagnetic field to each layer, a sublattice magnetic moment of therare-earth metal of said readout layer and a sublattice magnetic momentof the rare-earth metal of said auxiliary recording layer areantiparallel to each other.
 2. The magneto-optical recording mediumaccording to claim 1,wherein said readout layer has in-planemagnetization at room temperature such that in-plane magnetic anisotropyis stronger than perpendicular magnetic anisotropy and wherein the alloycomposition of said readout layer is such that, when a temperature ofsaid readout layer is raised to its compensation temperature, saidreadout layer has perpendicular magnetization in which the perpendicularmagnetic anisotropy is stronger than the in-plane magnetic anisotropy.3. The magneto-optical recording medium according to claim 1 or2,wherein an intermediate layer comprising a film having in-planemagnetization is formed at least between said readout layer and saidrecording layer or between said recording layer and said auxiliaryrecording layer.
 4. The magneto-optical recording medium according toclaim 1 or 2,wherein a radiating layer is formed on a surface of saidauxiliary recording layer where said recording layer is not formed. 5.The magneto-optical recording medium of claim 1 wherein said readoutlayer comprises a thin film of rare-earth transition metal alloy made ofrare-earth rich GdFeCo.
 6. The magneto-optical recording medium of claim5 wherein said thin film of said readout layer is approximately 50 nmthick.
 7. The magneto-optical recording medium of claim 1 wherein saidreadout layer comprises a thin film of rare-earth transition metal alloyof a composition Gd₀.26 (Fe₀.82 Co₀.18)₀.74.
 8. The magneto-opticalrecording medium of claim 1 wherein said recording layer comprises athin film of rare-earth transition metal alloy made of transition metalrich DyFeCo.
 9. The magneto-optical recording medium of claim 8 whereinsaid thin film of said recording layer is approximately 50 nm thick. 10.The magneto-optical recording medium of claim 1 wherein said recordinglayer comprises a thin film of rare-earth transition metal alloy of acomposition Dy₀.23 (Fe₀.78 Co₀.22)₀.77.
 11. The magneto-opticalrecording medium of claim 1 wherein said auxiliary recording layercomprises a thin film of rare-earth transition metal alloy made oftransition metal rich GdFeCo.
 12. The magneto-optical recording mediumof claim 8 wherein said thin film of said auxiliary recording layer isapproximately 50 nm thick.
 13. The magneto-optical recording medium ofclaim 1 wherein said auxiliary recording layer comprises a thin film ofrare-earth transition metal alloy of a composition Gd₀.17 (Fe₀.82Co₀.18)₀.83.
 14. The magneto-optical recording medium of claim 1 whereina protective film of AlN of a thickness of approximately 20 nm isdisposed on said auxiliary recording layer.
 15. The magneto-opticalrecording medium of claim 1 wherein said recording layer comprises athin film of rare-earth transition metal alloy made of rare-earth richDyFeCo of a thickness of approximately 50 nm and a composition of Dy₀.35(Fe₀.78 Co₀.22)₀.65.
 16. The magneto-optical recording medium of claim 1further comprising a radiating layer disposed on said auxiliaryrecording layer, said radiating layer being comprised of a materialselected from a group consisting of Au, Ag, Cu, SUS, Ta and Cr.
 17. Themagneto-optical recording medium of claim 1 further comprising at leastone intermediate layer disposed between at least one of said readoutlayer and said recording layer, and said recording layer and saidauxiliary recording layer.
 18. The magneto-optical recording medium ofclaim 17 wherein said at least one intermediate layer is of acomposition comprising FeCo.
 19. The magneto-optical recording medium ofclaim 2 wherein said readout layer has in-plane magnetization at roomtemperature, and a magnetic state which changes into perpendicularmagnetization as a temperature of the readout layer increases, and thereadout layer has perpendicular magnetization until the temperature ofthe readout layer is raised to a temperature substantially equal to itsCurie temperature.
 20. The magneto-optical recording medium of claim 3wherein said intermediate layer comprises a film having an in-planemagnetization in a temperature between room temperature and its Curietemperature.
 21. The magneto-optical recording medium of claim 1 whereinsaid auxiliary recording layer is made of a TM-rich material and saidrecording layer comprises a thin film of a composition Dy₀.23 (Fe₀.82Co₀.18)₀.77 having a thickness of approximately 50 nm and said readoutlayer is of a composition Gd_(x) (Fe₀.82 Co₀.18)_(1-x) wherein x is setin a range of 0.20<x<0.32.
 22. The magneto-optical recording medium ofclaim 1 wherein said readout layer is made of an RE-rich material andsaid auxiliary recording layer is of a composition Gd_(x) (Fe₀.82Co₀.18)_(1-x) wherein x is set in a range of 0.10<x<0.20.
 23. Themagneto-optical recording medium of claim 22 wherein said auxiliaryrecording layer has a thickness of not smaller than 10 nm.